CN117987691B - Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof - Google Patents
Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof Download PDFInfo
- Publication number
- CN117987691B CN117987691B CN202410404601.2A CN202410404601A CN117987691B CN 117987691 B CN117987691 B CN 117987691B CN 202410404601 A CN202410404601 A CN 202410404601A CN 117987691 B CN117987691 B CN 117987691B
- Authority
- CN
- China
- Prior art keywords
- resistant
- wear
- alloy
- corrosion
- nickel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 136
- 239000000956 alloy Substances 0.000 title claims abstract description 136
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 67
- 230000007797 corrosion Effects 0.000 title claims abstract description 56
- 238000005260 corrosion Methods 0.000 title claims abstract description 56
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 230000032683 aging Effects 0.000 claims abstract description 20
- 239000006104 solid solution Substances 0.000 claims abstract description 16
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 238000005242 forging Methods 0.000 claims description 32
- 238000003723 Smelting Methods 0.000 claims description 20
- 238000000034 method Methods 0.000 claims description 20
- 238000007670 refining Methods 0.000 claims description 14
- 229910052760 oxygen Inorganic materials 0.000 claims description 12
- 238000004321 preservation Methods 0.000 claims description 11
- 239000000243 solution Substances 0.000 claims description 11
- 239000011159 matrix material Substances 0.000 claims description 10
- 239000000463 material Substances 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- 239000002994 raw material Substances 0.000 claims description 7
- 238000005728 strengthening Methods 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 229910004261 CaF 2 Inorganic materials 0.000 claims description 6
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 6
- 230000008018 melting Effects 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 229910001868 water Inorganic materials 0.000 claims description 5
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052681 coesite Inorganic materials 0.000 claims description 3
- 229910052593 corundum Inorganic materials 0.000 claims description 3
- 229910052906 cristobalite Inorganic materials 0.000 claims description 3
- 239000007789 gas Substances 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- -1 mgO Inorganic materials 0.000 claims description 3
- 230000001105 regulatory effect Effects 0.000 claims description 3
- 239000000377 silicon dioxide Substances 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 229910052682 stishovite Inorganic materials 0.000 claims description 3
- 229910052905 tridymite Inorganic materials 0.000 claims description 3
- 229910001845 yogo sapphire Inorganic materials 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 238000012545 processing Methods 0.000 abstract description 8
- 230000007774 longterm Effects 0.000 abstract 1
- 239000002893 slag Substances 0.000 description 15
- 229910052757 nitrogen Inorganic materials 0.000 description 8
- 238000003754 machining Methods 0.000 description 7
- 230000005540 biological transmission Effects 0.000 description 5
- 229910052684 Cerium Inorganic materials 0.000 description 4
- 238000006477 desulfuration reaction Methods 0.000 description 4
- 230000023556 desulfurization Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 229910052739 hydrogen Inorganic materials 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 230000001737 promoting effect Effects 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910000997 High-speed steel Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910001315 Tool steel Inorganic materials 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 210000000078 claw Anatomy 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000001627 detrimental effect Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 229910001090 inconels X-750 Inorganic materials 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000000428 dust Substances 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910001055 inconels 600 Inorganic materials 0.000 description 1
- 229910001063 inconels 617 Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000779 smoke Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000001550 time effect Effects 0.000 description 1
Landscapes
- Manufacture And Refinement Of Metals (AREA)
Abstract
The wear-resistant corrosion-resistant nickel-base alloy comprises, by weight, 35.0% -40.0% of Cr,2.5% -4.0% of Al,0.02% -0.2% of Ce, 0.04% -0.2% of Mg, and the balance of Ni and unavoidable impurities. The alloy has good mechanical processing performance in a solid solution state, high strength, high hardness and good corrosion resistance in an aging state, and is suitable for long-term stable service under the working condition of more than 300 ℃. The invention also provides a manufacturing method and application of the wear-resistant corrosion-resistant nickel-based alloy.
Description
Technical Field
The invention belongs to the field of nickel-based alloys, and particularly relates to a wear-resistant corrosion-resistant nickel-based alloy, a manufacturing method and application thereof.
Background
Compared with the transmission piece in the conventional application scene, the transmission piece for the nuclear power equipment has higher design requirements and performance requirements. The spiral transmission part is a key part in the pressurized water reactor control rod driving mechanism and is used for converting the rotation of the motor into linear motion so as to realize the driving of the control rod assembly. The reliability of the screw driving part is directly related to the safety of the reactor, so that the screw in the screw driving part needs to have high temperature resistance, corrosion resistance, high strength and high hardness, and can be used for a long time in a high temperature environment, maintain good dimensional stability, and also needs to have good machining performance. At present, high-speed steel, tool steel or bearing steel commonly used for screw rod processing is insufficient in corrosion performance and mechanical performance under the service condition of about 300 ℃ in a nuclear power station, and can not meet the requirements of a rotary transmission part on reliability and control precision. The processing performance and mechanical properties of the existing various high-temperature corrosion-resistant materials, such as Incoloy800, inconel X-750, haslelloy and other nickel-based alloys, cannot completely match the processing requirements of screw rods of screw transmission parts. Therefore, the wear-resistant corrosion-resistant nickel-based alloy with good machining performance and mechanical property has positive significance for improving the safety and reliability of a nuclear reactor control system.
Disclosure of Invention
The invention aims to provide a wear-resistant corrosion-resistant nickel-based alloy with good machining performance and mechanical property. The invention also provides a manufacturing method and application of the wear-resistant corrosion-resistant nickel-based alloy.
According to an embodiment of one aspect of the present invention, there is provided a wear-resistant and corrosion-resistant nickel-base alloy, wherein the alloy comprises, by weight, 35.0% -40.0% of Cr,2.5% -4.0% of Al,0.02% -0.2% of Ce and 0.04% -0.2% of Mg, and the balance of Ni and unavoidable impurities.
In the alloy, cr is an important alloying element, can form an alpha phase with a Ni matrix, improves the strength, hardness, wear resistance, corrosion resistance and oxidation resistance of the alloy, has insufficient mechanical properties and chemical stability of a nickel-based alloy with too low Cr content, and can reduce the plasticity and toughness of the material when too high Cr content; further, the thermal conductivity of Cr is poor, and the excessively high content is unfavorable for improving the thermal deformation capacity of the alloy and reducing the thermal deformation yield of the alloy. The Al element can form a strengthening phase, so that the corrosion resistance and the oxidation resistance of the alloy are improved; if the Al element is too much, the plasticity and toughness of the alloy are not facilitated, meanwhile, inter-crystal corrosion is caused, and the impact toughness is reduced. Ce is favorable for promoting solidification and nucleation of the alloy, thereby realizing grain refinement, improving the uniformity of the structure and promoting desulfurization and deoxidation of the alloy structure to a certain extent. Proper amount of Mg is helpful for strengthening alloy grain boundary and improving hot workability; however, excessive Mg reduces the plasticity and toughness of the alloy.
Further, in some embodiments, the wear-resistant corrosion-resistant nickel-base alloy comprises less than or equal to 0.5% by weight of Fe, less than or equal to 0.1% by weight of Si, less than or equal to 0.1% by weight of Mn, less than or equal to 0.01% by weight of C, less than or equal to 20ppm by weight of O, and less than or equal to 100ppm by weight of N. Exceeding the limit of these elements forms a detrimental precipitated phase, with a significant adverse effect on the plasticity and toughness of the alloy.
Further, in some embodiments, the wear-resistant corrosion-resistant nickel-base alloy has an average grain size of not greater than 32 μm, and in a solid solution state, the wear-resistant corrosion-resistant nickel-base alloy satisfies: the tensile strength is less than or equal to 1500MPa, the elongation after fracture is more than or equal to 15 percent, and the hardness is less than or equal to 300HB; in an aging state, the structure of the wear-resistant corrosion-resistant nickel-based alloy comprises an alpha-Cr-rich phase matrix and a gamma' (Ni 3 Al) strengthening phase, and meets the following conditions: the tensile strength is more than or equal to 2000MPa, and the hardness is more than or equal to 50HRC. The solid solution state of the nickel-based alloy needs to have lower strength and hardness to improve the mechanical processing performance, while the aging state needs to have mechanical properties meeting the service requirements of a screw rod structure.
According to an embodiment of another aspect of the present invention, there is provided a method for manufacturing a wear-resistant and corrosion-resistant nickel-base alloy, for manufacturing the wear-resistant and corrosion-resistant nickel-base alloy provided in any one of the foregoing embodiments. The method comprises the following steps: 1) Providing raw materials according to the formula of the wear-resistant corrosion-resistant nickel-based alloy, and smelting to obtain an alloy cast ingot; 2) Carrying out electroslag remelting on the alloy ingot to obtain an electroslag ingot; 3) Forging the electroslag ingot to obtain an alloy forging, wherein the forging temperature is 1080-1150 ℃ and the final forging temperature is 830-950 ℃; 4) And carrying out solution treatment and aging treatment on the alloy forging to obtain a wear-resistant corrosion-resistant nickel-based alloy finished product.
Further, in some embodiments, the step 1) adopts vacuum induction smelting, including first refining and second refining, wherein the first refining inputs Ni and Cr bottom materials, the smelting temperature is 1520-1620 ℃, the vacuum degree is not more than 20Pa, and the smelting time is 0.05-0.3min/kg; adding the residual alloy elements into the secondary refining and stirring, wherein the smelting temperature is 1500-1600 ℃ and the smelting time is 0.4-0.6min/kg; after the raw materials are completely melted, the vacuum degree is controlled to be not more than 3Pa, and the temperature is regulated to 1480-1525 ℃ under the protection of argon gas for casting. The two refining processes can control O, N content and improve the uniformity of the components of the structure in the finished alloy product.
Further, in some embodiments, in the step 2), the electroslag component includes CaF 2、Al2O3、CaO、SiO2, mgO, and TiO 2, and the smelting temperature is 1675 ℃ to 1720 ℃ using an alloy or pure nickel base plate having the same composition as the wear-resistant and corrosion-resistant nickel base alloy. The electroslag remelting can effectively control S, P, H and other harmful elements, reduce and regulate nonmetallic inclusion, and improve surface quality.
Further, in some embodiments, in the step 3), the electroslag ingot is subjected to heat preservation at 1075 ℃ to 1200 ℃ for 40min to 150min before forging treatment.
Further, in some embodiments, in the step 3), the total deformation amount of the forging treatment is 55% -75%, and the forging pass is not more than 4 times.
Further, in some embodiments, in the step 4), the solution treatment temperature is 1050-1200 ℃, the heat preservation time is 40-180 min, and the water cooling is performed; the aging treatment temperature is 580-830 ℃, the heat preservation time is 180-480 min, and the air cooling is carried out.
According to an embodiment of a further aspect of the present invention, there is provided a wear-resistant and corrosion-resistant nickel-base alloy article manufactured by the manufacturing method of the wear-resistant and corrosion-resistant nickel-base alloy provided in any of the previous embodiments, the nickel-base alloy article being provided with a screw or nut.
Drawings
FIG. 1 is a flow chart of a method of manufacturing a wear-resistant corrosion-resistant nickel-base alloy in accordance with one embodiment;
FIG. 2a is a photograph of a metallographic structure of a wear-resistant corrosion-resistant nickel-base alloy according to an embodiment;
FIG. 2b is a photograph of a metallographic structure of a wear-resistant corrosion-resistant nickel-base alloy according to another embodiment.
The above drawings are provided for the purpose of explaining the present invention in detail so that those skilled in the art can understand the technical concept of the present invention, and are not intended to limit the present invention.
Detailed Description
The invention will now be described in further detail with reference to the accompanying drawings by means of specific examples.
Reference herein to "an embodiment" means that a particular feature, structure, or characteristic described in connection with the embodiment may be included in at least one embodiment herein. The appearances of such phrases in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments limited to the same embodiment. Those skilled in the art will appreciate that embodiments herein may be combined with other embodiments without structural conflict.
In the description herein, the meaning of "plurality" is at least two.
The traditional technical scheme of the nuclear reaction control rod driving mechanism adopts a claw type mechanism to drive and control the control rod, but the claw type scheme has larger volume and insufficient precision, and can not meet the design requirements of high precision and quick reaction of a small nuclear reactor at present. Therefore, a screw-driven screw-nut type control drive machine is a more technically advantageous solution for small nuclear reactors. However, materials such as high-speed steel, tool steel, bearing steel and the like commonly used in the current screw rod equipment cannot meet the requirements of heat resistance and corrosion resistance in a high-temperature service environment in a reactor, and the existing heat-resistant nickel-based alloys such as Incoloy800, inconel X-750, inconel600, inconel617, haynes230, haslelloyXR and HaslelloyN cannot meet the requirements of screw rod processing and service strength and processing performance.
In order to solve the above problems, an embodiment of one aspect of the present invention provides a wear-resistant and corrosion-resistant nickel-based alloy, which comprises the following components in weight ratio: 35.0% -40.0% of Cr,2.5% -4.0% of Al,0.02% -0.2% of Ce and 0.04% -0.2% of Mg, and the balance of Ni and unavoidable impurities. Specifically, the alloy structure components should further satisfy Fe less than or equal to 0.5, si less than or equal to 0.1, mn less than or equal to 0.1, C less than or equal to 0.01, O less than or equal to 20 ppm, and N less than or equal to 100 ppm.
In the alloy, cr is an important alloying element, can form an alpha phase with a Ni matrix, improves the strength, hardness, wear resistance, corrosion resistance and oxidation resistance of the alloy, has insufficient mechanical properties and chemical stability of a nickel-based alloy with too low Cr content, and can reduce the plasticity and toughness of the material when too high Cr content; further, the thermal conductivity of Cr is poor, and the excessively high content is unfavorable for improving the thermal deformation capacity of the alloy and reducing the thermal deformation yield of the alloy. The Al element can form a strengthening phase, so that the corrosion resistance and the oxidation resistance of the alloy are improved; if the Al element is too much, the plasticity and toughness of the alloy are not facilitated, meanwhile, inter-crystal corrosion is caused, and the impact toughness is reduced. Ce is favorable for promoting solidification and nucleation of the alloy, thereby realizing grain refinement, improving the uniformity of the structure and promoting desulfurization and deoxidation of the alloy structure to a certain extent. Proper amount of Mg is helpful for strengthening alloy grain boundary and improving hot workability; however, excessive Mg reduces the plasticity and toughness of the alloy. Fe, si, mn, C, O, N is an impurity element that forms a detrimental precipitated phase, and once excessive, adversely affects the plasticity and toughness of the alloy.
The alloy can be mechanically processed by heat treatment to reach a solid solution state, and then subjected to aging treatment to obtain higher strength and hardness. In the solid solution state, the performance of the alloy meets the requirement that the tensile strength is less than or equal to 1500MPa, the elongation after fracture is more than or equal to 15 percent, and the hardness is less than or equal to 300HB. In the aging state, the alloy structure matrix is an alpha-Cr-rich phase (Cr is dissolved in the Ni matrix) and the main strengthening phase is a gamma' phase, and the tensile strength is more than or equal to 2000Mpa, and the hardness is more than or equal to 50HRC.
The alloy has low hardness and good processability in a solid solution state, and can realize high-precision and high-efficiency processing of a screw rod and nut structure according to requirements; and good mechanical properties can be obtained after aging treatment, hardness and mechanical properties can be kept under service conditions of more than 300 ℃, and the alloy has good resistance to creep and good chemical stability. Cr element in the alloy matrix can form a protective layer by diffusing outwards along grain boundaries in a corrosive environment, so that the alloy has good resistance to high-temperature corrosion.
In a preferred embodiment, the alloy is produced by the following process, the flow of which is shown in FIG. 1:
Firstly, providing each component element according to the component proportion in the alloy formula, and refining twice by adopting a vacuum induction smelting method. Wherein, ni and Cr are added into the furnace for primary refining, the smelting temperature is 1520 ℃ to 1620 ℃, the vacuum degree is kept to be better than 20Pa, and the smelting is carried out according to the time of 0.05 min/kg to 0.3 min/kg. Adding other alloy elements into a secondary refining phase furnace, fully stirring mechanically and electromagnetically after charging, smelting at 1500-1600 ℃ for 0.4-0.6min/kg, controlling vacuum degree to be better than 3.0Pa after the alloy raw materials are completely melted, charging argon for protection, standing and regulating temperature to 1480-1525 ℃, and then casting uniformly at a slow speed to obtain alloy ingots. The two refining steps are beneficial to controlling O, N content in the alloy and improving uniformity of alloy structure components.
And then electroslag remelting smelting is carried out on the alloy ingot. The electroslag with the components including CaF 2、Al2O3、CaO、SiO2, mgO and TiO 2 is adopted, and the proportion components in the electroslag are adjusted according to the impurity components in the raw materials. Specifically, in order to better remove the elements such as S, the proportion of the viscosity of a molten slag pool to CaO needs to be properly controlled, the degassing effect can be improved by improving the viscosity, but the time and the cost can be increased, the alkalinity of slag can be improved by CaO, the desulfurization efficiency is improved, the conductivity is reduced, the CaO is easy to absorb water, and H and O are easy to be brought if the proportion is too high; caF 2 can reduce the melting point, viscosity and surface tension of slag, but CaF 2 has higher conductivity and is easy to release harmful gas and smoke dust; al 2O3 can reduce the conductivity of slag and reduce the power consumption, but can improve the melting temperature and viscosity and reduce the desulfurization effect, and the general proportion is not more than 50%; mgO can form a semi-solidified film on the surface of the slag bath, prevents the slag bath from absorbing hydrogen and prevents the variable oxides in the slag bath from transferring oxygen to a metal molten pool, so that the H, O, N content is reduced, but MgO can cause the viscosity to be improved, and the proportion is usually not more than 15%; siO 2 can reduce the melting point of slag, improve high-temperature plasticity and reduce the conductivity of slag, but can cause volatilization loss of CaF 2; tiO 2 can be used as a conductive slag ignition agent with CaF 2, but can be used as a valence-changing oxide to play a role in transferring oxygen supply. The person skilled in the art can make a reasonable choice of slag system proportions according to the impurity components in the raw materials and the refining requirements in combination with the principles described above. According to a large number of research experiments, the electroslag remelting smelting temperature is determined to be 1675-1720 ℃, and when the temperature is lower than 1675 ℃, the speed of molten alloy drops passing through a slag bath is too slow, so that the smelting time and energy consumption are too high; when the temperature is higher than 1720 ℃, the alloy melt is at risk of boiling, which can cause loss of Cr and other elements, and can cause too high speed of the alloy melt drop passing through a slag bath, so that impurities can not be removed sufficiently. In the electroslag remelting process, nickel alloy or pure nickel with the same components as the alloy finished product is used as a bottom plate, the bottom plate is used for separating an electroslag ingot from a die, and the bottom plate is cut off from the electroslag ingot after the electroslag remelting. The depth, current and voltage of the slag pool are controlled by adjusting the size of the crystallizer, the weight of the slag and other means so as to keep the stability of the electroslag remelting smelting process, and hot feeding is carried out for 3-5 times before smelting is finished, so that the high-purity electroslag ingot is finally obtained. The specific process parameters in the electroslag remelting process can be reasonably selected by a person skilled in the art according to the characteristics of the model, the size and the like of the electroslag remelting equipment.
Next, forging the electroslag ingot. The heat preservation temperature is 1075-1200 ℃ before forging, the heat preservation time is 40-150min, the forging start temperature is 1080-1150 ℃, the final forging temperature is 830-950 ℃, and air cooling is carried out after forging. Wherein the total deformation of the nut blank is about 56% and the total deformation of the lead screw blank is about 73% and no more than 6 passes, and in a further preferred embodiment no more than 4 passes. In a preferred embodiment, the reduction per pass is no more than 12%.
Finally, heat treatment is performed on the alloy Jin Duanjian, wherein the heat treatment comprises solution treatment and aging treatment. Wherein the heat preservation temperature of the solution treatment is 1050-1200 ℃, the heat preservation time is 40-80 min, and the water cooling is performed after the heat preservation is finished. The solution treatment is used for forming the alloy into a uniform supersaturated solid solution, so that the internal stress generated in the forging process is eliminated, the hardness of the alloy is reduced, the subsequent machining is facilitated, and the formation of uniform and fine precipitated phases in the subsequent aging treatment process is facilitated. The aging treatment temperature is 580-830 ℃, the heat preservation time is 180-480 min, and the air cooling is carried out after the heat preservation is finished. The aging treatment can form a uniformly dispersed precipitated phase which is mainly gamma' in an alloy structure, so that the mechanical property of the alloy is improved.
The heat-treated nickel-base alloy is tested according to GB/T228, GB/T230.1, GB/T231.1 and other standards, and the requirements are satisfied: the tensile strength of the solid solution state alloy is less than or equal to 1500MPa, the elongation after fracture is more than or equal to 15%, and the hardness is less than or equal to 300HB; the tensile strength of the aged alloy is more than or equal to 2000MPa, and the hardness is more than or equal to 50HRC.
In a preferred embodiment, the composition of the electroslag ingot smelted according to the electroslag remelting process in the previous embodiment is detected as: cr40.0%, al3.3%, ce0.05%, mg0.06%, fe0.30%, si0.07%, mn0.02%, C0.009%, P0.001%, S0.001%, and Ni balance O, N were not detected. And (3) preserving the heat for 150min at 1100+/-25 ℃, performing four-pass forging, wherein the forging temperature is 1100 ℃, the final forging temperature is 830 ℃, and the total deformation is 75%, so that the alloy forging with the straightness ranging from 0.7 mm/m to 0.8mm/m is obtained. Carrying out solution treatment at 1140 ℃ for 70min to obtain a solid solution state alloy sample, wherein the metallographic structure of the solid solution state alloy sample is shown in figure 2a, and the grain size of the matrix is 8 grade (according to GB/T6394-2017); the tensile strength of 1050MPa, the elongation of 26% and the hardness of 253HB were measured by cutting the sample into standard samples and performing a tensile test. Aging the solid solution state alloy sample at 725 ℃ for 5 hours to obtain an aging state alloy; the sample is cut into a standard sample, tensile strength 2018MPa, elongation after break 4% and sample hardness 54.4HRC are measured by tensile test.
In another preferred embodiment, the composition of the electroslag ingot smelted according to the electroslag remelting process in the previous embodiment is detected as: cr39.9%, al3.1%, ce0.06%, mg0.08%, fe0.33%, si0.09%, mn0.03%, C0.009%, P0.001%, S0.0009%, ni balance O, N. Preserving the heat for 40min at 1175+/-25 ℃, performing four-pass forging, wherein the forging temperature is 1150 ℃, the final forging temperature is 950 ℃, and the total deformation is 75%, so that the alloy forging with the straightness of 0.7-0.8mm/m is obtained. Carrying out solution treatment at 1170 ℃ for 70min to obtain a solid solution state alloy sample, wherein the metallographic structure of the solid solution state alloy sample is shown in figure 2b, and the grain size of the matrix is 8 grade (according to GB/T6394-2017); the tensile strength of 1049MPa, the elongation of 28.5% and the hardness of 271HB were measured by cutting into standard samples and carrying out tensile test. Aging the solid solution state alloy sample at 740 ℃ for 6 hours to obtain an aging state alloy; the tensile strength 2005MPa, the elongation after break 4% and the sample hardness 52HRC were measured by cutting into standard samples and carrying out tensile test. The alloy can be used for manufacturing screw rods. In yet another embodiment, the electroslag ingot composition, forging parameters are the same as the heat treatment parameters, the total deformation of the forging is 55%, and the alloy is used to make nuts.
In an alternative embodiment, the composition of the electroslag ingot smelted according to the electroslag remelting process in the previous embodiment is detected as: 37.4% of Cr, 2.66% of Al, 0.17% of Ce, 0.18% of Mg, 0.153% of Fe, 0.051% of Si, 0.018% of Mn, 0.0075% of C, 0.0013% of P, 0.0007% of S and the balance of Ni, O, N are not detected. In the embodiment, the addition amount of Ce and Mg is close to the upper limit of 0.2%, the obtained alloy has better structural uniformity, the highest grain size can reach 9.5 grade (according to GB/T6394-2017), but the tensile strength and the hardness under the influence of Ce and Mg are close to the lower limit of performance requirements of 2000MPa and 50HRC, the elongation is about 3.5%, and the alloy needs to be compensated by cold work hardening in the subsequent machining process. When Ce or Mg exceeds the upper limit of 0.2%, the tensile strength and hardness in the aged state are not satisfactory. The Cr content is in the range of 35% -55%, the mechanical properties of the aging nickel-base alloy are approximately linearly changed under the influence of the solid solution and gamma phase production amount, the performance data according to the embodiment are extrapolated in combination with engineering experience, when the Cr content is lower than 35%, the mechanical properties of the alloy cannot meet the requirements by adjusting other alloy components (such as reducing the Ce and Mg contents), and when the Cr content is higher than 40%, the plasticity and toughness of the alloy are reduced, so that the machining requirements cannot be met by adjusting other alloy components.
In another alternative embodiment, the composition of the electroslag ingot smelted according to the electroslag remelting process in the previous embodiment is detected as: 39.4% of Cr, 3.92% of Al, 0.025% of Ce, 0.10% of Mg, 0.472% of Fe, 0.052% of Si, 0.022% of Mn, 0.0076% of C, 0.0019% of P, 0.0008% of S and the balance of Ni, O, N are not detected. In the embodiment, the Ce element is close to the lower limit value of 0.02%, the mechanical property and the hardness of the alloy in the time-effect state meet the design requirements, but the risks of sporadic coarse crystals in the structure and uneven axial hardness distribution of the finished product start to increase. When Ce is below the lower limit of 0.02%, significant non-uniformity of the material structure may occur, which may lead to difficulties in subsequent bar machining. The alloy manufactured by the method has good strength, hardness and wear resistance, can keep good mechanical property and corrosion resistance at the temperature of more than 300 ℃, and has good dimensional stability. The screw and nut in the screw nut type control driving mechanism manufactured by adopting the wear-resistant corrosion-resistant nickel-based alloy has the advantages of high precision and good reliability, can stably work for a long time under the service condition of more than 300 ℃ in a nuclear reactor, prolongs the service life of the nuclear reactor control mechanism, and improves the safety and reliability of a control system.
The above-described embodiments are intended to provide further detailed description of the present invention so that those skilled in the art can understand the technical concept of the present invention. Within the scope of the present disclosure, the material compositions or method steps involved are optimized or replaced equivalently, and the implementation manners of the different embodiments are combined on the premise that no structural and principle conflict occurs, which falls within the protection scope of the present disclosure.
Claims (8)
1. The wear-resistant corrosion-resistant nickel-base alloy is characterized by comprising, by weight, 35.0% -40.0% of Cr,2.5% -4.0% of Al,0.02% -0.2% of Ce, 0.04% -0.2% of Mg and the balance of Ni and unavoidable impurities, wherein among the unavoidable impurities, fe is less than or equal to 0.5%, si is less than or equal to 0.1%, mn is less than or equal to 0.1%, C is less than or equal to 0.01%, O is less than or equal to 20ppm, and N is less than or equal to 100ppm;
The grain size of the wear-resistant corrosion-resistant nickel-based alloy matrix is 8-9.5, and in a solid solution state, the wear-resistant corrosion-resistant nickel-based alloy meets the following conditions: the tensile strength is less than or equal to 1500MPa, the elongation after fracture is more than or equal to 15 percent, and the hardness is less than or equal to 300HB;
in an aging state, the structure of the wear-resistant corrosion-resistant nickel-based alloy comprises an alpha-Cr-rich phase matrix and a gamma' strengthening phase, and meets the following conditions: the tensile strength is more than or equal to 2000MPa, the hardness is more than or equal to 50HRC, and the elongation after fracture is more than or equal to 3.5 percent.
2. A method of manufacturing a wear-resistant corrosion-resistant nickel-base alloy, characterized in that the method of manufacturing a wear-resistant corrosion-resistant nickel-base alloy according to claim 1 is used for manufacturing a wear-resistant corrosion-resistant nickel-base alloy, and comprises the steps of:
1) Providing raw materials according to the formula of the wear-resistant corrosion-resistant nickel-based alloy, and smelting to obtain an alloy cast ingot;
2) Carrying out electroslag remelting on the alloy ingot to obtain an electroslag ingot;
3) Forging the electroslag ingot to obtain an alloy forging, wherein the forging temperature is 1080-1150 ℃ and the final forging temperature is 830-950 ℃;
4) And carrying out solution treatment and aging treatment on the alloy forging to obtain a wear-resistant corrosion-resistant nickel-based alloy finished product.
3. The method for producing a wear-resistant and corrosion-resistant nickel-base alloy according to claim 2, wherein the step 1) adopts vacuum induction melting, comprising a first refining and a second refining, wherein the first refining is performed by adding Ni and Cr base materials, the melting temperature is 1520 ℃ to 1620 ℃, the vacuum degree is not more than 20Pa, and the melting time is 0.05 min/kg to 0.3min/kg; adding the residual alloy elements into the secondary refining and stirring, wherein the smelting temperature is 1500-1600 ℃ and the smelting time is 0.4-0.6min/kg; after the raw materials are completely melted, the vacuum degree is controlled to be not more than 3Pa, and the temperature is regulated to 1480-1525 ℃ under the protection of argon gas for casting.
4. The method of producing a wear-resistant and corrosion-resistant nickel-base alloy according to claim 2, wherein in step 2), the electroslag component includes CaF 2、Al2O3、CaO、SiO2, mgO, and TiO 2, and the smelting temperature is 1675 ℃ to 1720 ℃ using an alloy or pure nickel base plate of the same composition as the wear-resistant and corrosion-resistant nickel-base alloy.
5. The method for producing a wear-resistant and corrosion-resistant nickel-base alloy according to claim 2, wherein in the step 3), the electroslag ingot is subjected to heat-retaining treatment at 1075 ℃ to 1200 ℃ for 40min to 150min before the forging treatment.
6. The method of producing a wear-resistant and corrosion-resistant nickel-base alloy according to claim 2 or 5, wherein in step 3), the total deformation amount of the forging process is 55 to 75% and the forging passes are not more than 4 times.
7. The method for producing a wear-resistant and corrosion-resistant nickel-base alloy according to claim 2, wherein in the step 4), the solution treatment temperature is 1050 ℃ to 1200 ℃, the holding time is 40min to 180min, and the solution is cooled by water cooling; the aging treatment temperature is 580-830 ℃, the heat preservation time is 180-480 min, and the air cooling is carried out.
8. A wear-resistant and corrosion-resistant nickel-base alloy article, characterized in that it is manufactured by the manufacturing method of a wear-resistant and corrosion-resistant nickel-base alloy according to any one of claims 2 to 7, said wear-resistant and corrosion-resistant nickel-base alloy article being configured as a screw or nut.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410404601.2A CN117987691B (en) | 2024-04-07 | 2024-04-07 | Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410404601.2A CN117987691B (en) | 2024-04-07 | 2024-04-07 | Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN117987691A CN117987691A (en) | 2024-05-07 |
| CN117987691B true CN117987691B (en) | 2024-06-18 |
Family
ID=90890845
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202410404601.2A Active CN117987691B (en) | 2024-04-07 | 2024-04-07 | Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN117987691B (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104178648A (en) * | 2014-09-12 | 2014-12-03 | 重庆材料研究院有限公司 | Preparation method of nonmagnetic corrosion-resistant nickel-chromium-base bearing alloy |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3401711A1 (en) * | 1984-01-19 | 1985-07-25 | VEB Edelstahlwerk 8. Mai 1945 Freital, DDR 8210 Freital | Process for producing high-temperature creep-resistant nickel alloys in an electron beam furnace |
| JP2003001344A (en) * | 2001-06-25 | 2003-01-07 | Nippon Steel Corp | Mold for press forming |
| JP2005082885A (en) * | 2003-09-11 | 2005-03-31 | Daido Steel Co Ltd | Component of diesel engine |
| WO2005078148A1 (en) * | 2004-02-12 | 2005-08-25 | Sumitomo Metal Industries, Ltd. | Metal tube for use in carburizing gas atmosphere |
-
2024
- 2024-04-07 CN CN202410404601.2A patent/CN117987691B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104178648A (en) * | 2014-09-12 | 2014-12-03 | 重庆材料研究院有限公司 | Preparation method of nonmagnetic corrosion-resistant nickel-chromium-base bearing alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN117987691A (en) | 2024-05-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US11859262B2 (en) | Large-sized high-Nb superalloy ingot and smelting process thereof | |
| CN108526422B (en) | Production method of high-strength high-conductivity heat-resistant copper alloy | |
| CN110964936B (en) | Production process of high-strength corrosion-resistant aluminum alloy for power line hardware | |
| CN1818109A (en) | Copper alloy materials with high-strength and conducting performances and production thereof | |
| JP7471520B2 (en) | Manufacturing method for low carbon nitrogen containing austenitic stainless steel rod | |
| CN114645162A (en) | Manufacturing method of fine-grain homogeneous disc forging of high-temperature alloy difficult to deform | |
| CN110592435A (en) | Lightweight aluminum alloy profile | |
| CN100532599C (en) | Fatigue resistant Cu-Ti alloy and producing method thereof | |
| CN115287503B (en) | Aluminum-beryllium intermediate alloy and preparation method thereof | |
| CN114086027A (en) | High-temperature softening resistant Cu-Ni-Sn series high-strength high-elasticity copper alloy and preparation method thereof | |
| CN115094263B (en) | Alterant alloy for copper-chromium-zirconium series alloy, preparation method and application thereof | |
| CN1138017C (en) | Middle-alloy chromium series hot die steel | |
| CN117987691B (en) | Wear-resistant corrosion-resistant nickel-based alloy and manufacturing method and application thereof | |
| CN110273114B (en) | Wear-resistant iron-silicon-chromium alloy and preparation method thereof | |
| CN112226636A (en) | Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate | |
| CN114875270B (en) | Tin-phosphor bronze alloy and preparation method thereof | |
| CN114672675B (en) | Nickel-rich nickel-titanium alloy gear and preparation method thereof | |
| CN110629128A (en) | FeCrAlZr cladding material and preparation method thereof | |
| CN111809074B (en) | Lanthanum-carbon-magnesium composite material, tellurium-copper alloy material and preparation method thereof | |
| CN111549257B (en) | Zinc alloy with low cost and good tensile strength and preparation method thereof | |
| CN111893356A (en) | Preparation process of high-strength rare earth aluminum alloy | |
| CN109778073B (en) | Free-cutting steel for automobile synchronizer and preparation method thereof | |
| CN108642400A (en) | A kind of high-performance carbide mold materials and preparation method thereof | |
| CN115874075B (en) | Low-impurity and easy-to-polish zinc alloy and preparation process thereof | |
| CN115404383B (en) | High-strength nickel-based alloy wire for nuclear power, manufacturing method and application |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant |