WO2021219056A1 - 一种高强度不锈钢转子及其制备方法 - Google Patents

一种高强度不锈钢转子及其制备方法 Download PDF

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Publication number
WO2021219056A1
WO2021219056A1 PCT/CN2021/090831 CN2021090831W WO2021219056A1 WO 2021219056 A1 WO2021219056 A1 WO 2021219056A1 CN 2021090831 W CN2021090831 W CN 2021090831W WO 2021219056 A1 WO2021219056 A1 WO 2021219056A1
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Prior art keywords
forging
stainless steel
blank
rotor
temperature
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PCT/CN2021/090831
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English (en)
French (fr)
Inventor
刘振宝
梁剑雄
王晓辉
孙永庆
王长军
杨志勇
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钢铁研究总院
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Priority to JP2021576893A priority Critical patent/JP7236569B2/ja
Priority to US17/638,179 priority patent/US11951530B2/en
Publication of WO2021219056A1 publication Critical patent/WO2021219056A1/zh
Priority to ZA2022/03034A priority patent/ZA202203034B/en

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/002—Hybrid process, e.g. forging following casting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/008—Incremental forging
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
    • B21J5/08—Upsetting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K1/00—Making machine elements
    • B21K1/28—Making machine elements wheels; discs
    • B21K1/32—Making machine elements wheels; discs discs, e.g. disc wheels
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01C—MEASURING DISTANCES, LEVELS OR BEARINGS; SURVEYING; NAVIGATION; GYROSCOPIC INSTRUMENTS; PHOTOGRAMMETRY OR VIDEOGRAMMETRY
    • G01C19/00—Gyroscopes; Turn-sensitive devices using vibrating masses; Turn-sensitive devices without moving masses; Measuring angular rate using gyroscopic effects
    • G01C19/02—Rotary gyroscopes
    • G01C19/04—Details
    • G01C19/06—Rotors

Definitions

  • the invention relates to the technical field of thermal processing of metal materials, in particular to a high-strength stainless steel rotor and a preparation method thereof.
  • High-strength stainless steel has high strength, toughness and corrosion resistance. It is an excellent structural material and is widely used in petroleum, chemical, civil ship, aerospace, civil aircraft and other fields. At present, high-strength stainless steel forgings are widely used, and the forging process has been studied.
  • the high-speed rotor is an important part of the gyroscope.
  • High-strength stainless steel has the characteristics of high strength, high toughness, high dimensional stability, corrosion resistance, etc., so it can achieve better service performance when used to manufacture high-speed rotors.
  • 1Cr18Ni9Ti stainless steel is used to prepare bar materials through a free forging process, and then a high-speed rotor is prepared through cutting processing. The amount of cutting processing is relatively large, which greatly wastes raw materials and increases costs.
  • the metal streamlines of the rotor machined by the bar material are not closed, and there are safety hazards during use; in addition, the strength of the rotor made of 1Cr18Ni9Ti stainless steel is only 560MPa, and the low strength leads to a short service life.
  • the embodiment of the present invention aims to provide a high-strength stainless steel rotor and a preparation method thereof, to solve the problems of low strength of the rotor, short service life, and high cost of cutting materials in the forging process. .
  • a high-strength stainless steel rotor The element composition of the rotor is calculated by mass percentage: C: 0.03% ⁇ 0.050%, Cr: 14.90% ⁇ 15.80%, Ni: 5.00% ⁇ 5.70%, Cu: 2.20% ⁇ 2.80%, Nb +Ta: 0.35% ⁇ 0.44%, Mo: 0.45% ⁇ 0.54%, V: 0.06% ⁇ 0.10%, Si: 0.20% ⁇ 0.60%, Mn: 0.40% ⁇ 0.80%, P ⁇ 0.010%, S ⁇ 0.010% , O ⁇ 0.003%, the rest is iron and inevitable impurity elements.
  • the element composition of the rotor is calculated by mass percentage: C: 0.043%, Cr: 15.4%, Ni: 5.35%, Cu: 2.52%, Nb+Ta: 0.41%, Mo: 0.53%, V: 0.08% , Si: 0.25%, Mn: 0.46%, P: 0.005%, S ⁇ 0.010%, O ⁇ 0.003%, the rest is iron and inevitable impurity elements.
  • a method for preparing a high-strength stainless steel rotor for preparing the above-mentioned high-strength stainless steel rotor includes the following steps:
  • Step 1 Prepare rotor stainless steel blank
  • Step 2 The rotor stainless steel blank is heated for the first time and then subjected to free forging, and then subjected to the first annealing and surface treatment after the free forging, to obtain a forging blank;
  • Step 3 The forging blank is heated for a second time, die forging is performed after the second heating, and annealing treatment and solution treatment are performed for the second time after die forging to obtain a forging;
  • Step 4 A high-strength stainless steel rotor is made from the forgings after rough machining, aging treatment and finishing.
  • the length of the rotor stainless steel blank is 450-480 mm, and the diameter is ⁇ 350 mm.
  • the first heating process is as follows: the gas furnace is heated to 750°C, the billet is charged into the gas furnace, the temperature is maintained for 1.5-2h, and then the temperature is raised to 1140-1170°C at a rate of 200-300°C/h , Keep for 2 ⁇ 3h.
  • free forging includes two upsetting and one drawing of the rotor stainless steel blank, and one upsetting to the diameter Pull up to the diameter Secondary Pier Thick to Diameter
  • the free forging and forging temperature of rotor stainless steel blank is 1140 ⁇ 1170°C, and the final forging temperature is greater than or equal to 900°C.
  • the blank is pile-cooled to 300°C and then dispersed, and air-cooled to room temperature.
  • the first annealing treatment is to put the free-forged blank into a resistance furnace to heat it to 640°C to 660°C, keep it for 12 to 20 hours, and then cool it to room temperature along with the furnace to obtain a forging billet.
  • the second heating is: the gas furnace is heated to 750°C, the forging billet is loaded, the temperature is kept for 1.5 to 3 hours, and then the temperature is raised to 1120°C to 1150°C at a rate of 100 to 150°C/h, and the temperature is kept warm. 1 ⁇ 2h.
  • the die forging process is: putting the forging blank after the second heating into a die forging machine for die forging; the initial forging temperature of die forging is 1120-1140°C, and the final forging temperature is greater than or equal to 900°C ; After die forging, the forging billet is air-cooled to room temperature.
  • the deformation mode of the lower die pressing forging is adopted, and the pressing deformation is performed 5 times; the 5 pressing deformations are:
  • the upper die is pressed down for the blank with a pressure of more than 5,000 tons;
  • the forging billet was pressed under a pressure of 4000 tons and held for 30-40 seconds.
  • the thickness direction of the obtained forging blank is reduced from 280 mm to 100-120 mm, and the forging ratio is greater than 2.
  • the second annealing treatment is to put the forging billet after die forging into a resistance furnace, raise the temperature to 640°C-660°C, keep the temperature for 25h-30h, and cool the furnace to room temperature.
  • the solution treatment is to heat the forging blank after the second annealing treatment in a resistance furnace to 1035-1045°C, keep it for 1 to 1.5 hours, and cool the forging blank to below 32°C after the heat preservation is completed. Prepare forgings.
  • the aging treatment is to put the rough-processed forgings into a resistance furnace to heat to 550-560°C, keep the temperature for 4 to 4.5 hours, and cool to room temperature in air.
  • the surface quality of the high-strength stainless steel rotor obtained after the finishing process reaches Ra1.6.
  • the present invention can achieve at least one of the following beneficial effects:
  • the present invention adopts high-strength stainless steel material, through the combined use of two forging processes of free forging and die forging, as well as heating before free forging and die forging, and annealing treatment after free forging and die forging respectively, and annealing at the last time
  • the tensile strength R m of the rotor is not less than 1100MPa
  • the yield strength Rp 0.2 is not less than 1000MPa
  • the elongation after fracture A is not less than 15%
  • the reduction of area Z is not less than 55%
  • the hardness is not less than 36HRC, the strength of the existing rotor is increased by more than 500MPa, and the service life of the rotor is improved.
  • the present invention adopts the preparation process of first free forging and then die forging.
  • the forging ratio of free forging is greater than 3, the forging ratio of die forging is greater than 2, and the cumulative forging ratio of free forging and die forging is greater than 5, and both horizontal and vertical directions are large.
  • Deformation the austenite grain size is fine, the grain size is larger, and the grain size is fine (above 6), so that the horizontal and vertical mechanical properties of the forging are consistent, and the fatigue life of the high-speed rotating parts of the rotor is improved, and it is safe and reliable. Sexual improvement.
  • the free forging of the blank in the present invention includes two upsetting and one lengthening processes.
  • the blank is upset to diameter for the first time Pull up to the diameter Second pier thick to diameter
  • free forging is started.
  • the open forging temperature of the blank free forging is 1140 to 1170°C, preferably 1140 to 1150°C.
  • the purpose of two piercing and one drawing is to make the blank produce a larger amount of deformation and obtain smaller grains, and at the same time, the blank obtains uniform horizontal and vertical grain sizes.
  • the first annealing treatment after free forging and the second annealing treatment after die forging are adopted.
  • the temperature range of opening forging and final forging is strictly controlled.
  • the forging temperature is greater than 900°C;
  • the die forging opening temperature is 1120 ⁇ 1140°C, and the die forging final forging temperature is greater than 900°C.
  • the forging blank at this temperature has good thermoplasticity. Controlling the deformation amount and deformation size each time is beneficial to deformation and ensures the forging The plasticity of the process material can achieve a larger forging ratio without cracks and other defects.
  • the rough machining of the forging in the present invention can reduce tool loss after solution treatment, and leave a small finishing allowance. Finishing after aging can reduce tool wear due to increased material hardness.
  • a combination of free forging and die forging is adopted to obtain a closed streamline of metal streamlines along the shape of the forging.
  • the overall metal streamline of the prepared rotor is closed, which improves the fatigue resistance and use of the forging.
  • Safety suitable for service cycle of more than 10 years.
  • the forgings of the present invention have a small amount of cutting processing, saving the amount of raw materials used, effectively reducing the cost, and avoiding the problems of direct cutting and processing of bars into the shape of forgings by traditional technology, large processing volume, waste of raw materials, and product consistency Good, the pass rate reaches 100%.
  • Figure 1 is a schematic diagram of a rotor die forging
  • Figure 2 is a schematic diagram of the rotor
  • Figure 3 shows the grain size of the core of the high-speed rotor in Example 1;
  • Figure 4 shows the grain size at the edge of the high-speed rotor in Example 1;
  • Figure 5 shows the grain size of the high-speed rotor core in Comparative Example 1
  • Figure 6 shows the grain size at the edge of the high-speed rotor in Comparative Example 1.
  • a specific embodiment of the present invention discloses a high-strength stainless steel rotor whose element composition is calculated by mass percentage: C: 0.03% ⁇ 0.050%, Cr: 14.90% ⁇ 15.80%, Ni: 5.00% ⁇ 5.70%, Cu: 2.20% to 2.80%, Nb+Ta: 0.35% to 0.44%, Mo: 0.45% to 0.54%, V: 0.06% to 0.1%, Si: 0.20% to 0.60%, Mn: 0.40% to 0.80%, P ⁇ 0.010%, S ⁇ 0.010%, O ⁇ 0.003%, the rest is iron and unavoidable impurity elements.
  • Ni is added to obtain a martensitic structure
  • the strengthening element Cu (2.20-2.80%) is added to precipitate the second phase ⁇ -Cu
  • Nb is added to obtain the NbC precipitate phase
  • Mo The addition of cyanide has a solid solution strengthening effect.
  • P and S are reduced to below 0.01%
  • O is reduced to below 0.003%
  • the alloy ratio of Cr element is 14.90-15.80 %.
  • the present invention provides a method for preparing a high-strength stainless steel rotor, which includes the following steps:
  • Step 1 Prepare rotor stainless steel blank
  • Step 2 Free forging is performed on the blank after the first heating, and the first annealing and surface treatment are performed after the free forging to obtain a forging blank;
  • the first heating process is as follows: the gas furnace is heated to 750°C, the billet is loaded into the gas furnace, and the temperature is maintained for 1.5 to 2 hours, and then the temperature is raised to 1140 to 1170°C at a rate of 200 to 300°C/h, and the temperature is maintained for 2 to 3 hours.
  • Free forging includes two upsetting and one drawing of the blank, and one upsetting to the diameter Pull up to the diameter Secondary Pier Thick to Diameter
  • the open forging temperature of the blank is 1140 ⁇ 1170°C, and the final forging temperature is greater than or equal to 900°C.
  • the blank After forging, the blank is pile-cooled to 300°C and then dispersed and cooled to room temperature in air; the first annealing treatment is to put the blank after free forging into the resistance furnace It is heated to 640°C ⁇ 660°C, kept for 12h ⁇ 20h, and cooled to room temperature along with the furnace to obtain the forging billet.
  • Step 3 The forging blank is heated for the second time, die forging is performed after the second heating, and annealing treatment and solution treatment are performed for the second time after die forging to obtain a forging;
  • the second heating is: the gas furnace is heated to 750°C, the forging billet is loaded, and the temperature is kept for 1.5 to 3 hours, and then the temperature is raised to 1120°C to 1150°C at a rate of 100 to 150°C/h, and the temperature is kept for 1 to 2 hours.
  • the die forging process is as follows: the forging blank is placed in a die forging machine for die forging, the initial forging temperature is 1120-1140°C, the final forging temperature is greater than or equal to 900°C, and the forging blank is air-cooled to room temperature after forging.
  • the second annealing treatment is to put the forging billet after die forging in a resistance furnace, heat up to 640°C ⁇ 660°C, keep it for 25h ⁇ 30h, and cool the furnace to room temperature.
  • the solution treatment is to heat the forging billet after the second annealing treatment in a resistance furnace to 1035 ⁇ 1045°C, keep it for 1 ⁇ 1.5h, and air-cool to below 32°C to obtain forgings.
  • Step 4 The forgings are processed by rough machining, aging treatment and finishing to obtain a high-strength stainless steel rotor;
  • the aging treatment is to put the rough-processed forgings in a resistance furnace to heat to 550-560°C, keep the temperature for 4 to 4.5 hours, and cool to room temperature in air to prepare the rotor.
  • the prepared size is diameter
  • the high-strength stainless steel bar is used for cutting the billet with a length of 450-480mm to remove surface burrs.
  • the present invention rounds R20 on the two end faces of the blank.
  • step 2 the specific steps are as follows:
  • Step 21 The billet is heated for the first time in a gas furnace
  • the billet After the gas furnace is heated to 750 ⁇ 760°C, the billet is loaded and kept for 1.5 ⁇ 2h, and then the temperature is raised to 1140 ⁇ 1170°C at a rate of 200 ⁇ 300°C/h, and the temperature is kept for 2 ⁇ 3h. Choose to load the billet at 750-760°C so that the billet can quickly pass through the 400-470°C brittle temperature range and reduce the brittleness of the billet.
  • the blank is kept in the temperature range of 400 ⁇ 470°C for a long time, strengthening phase will be precipitated in the structure, which will increase the tendency of the material to crack due to the influence of internal thermal stress.
  • the heating rate of the gas furnace in the prior art is 100°C/h
  • the heating rate of the billet in the present invention is 200-300°C/h.
  • shortening the heating rate can also inhibit the growth of austenite grains of the stainless steel billet at high temperatures, increase the strength of the billet, and reduce the plasticity of the billet; the billet is kept at 1140 ⁇ 1170°C for 2 ⁇ 3h, which can ensure the temperature and structure of the billet before forging.
  • the uniformity is
  • Step 22 Free forging of the blank
  • Billet free forging includes two pier roughing and one drawing process.
  • the blank is upset to diameter for the first time Pull up to the diameter Second pier thick to diameter
  • free forging is started.
  • the open forging temperature of the blank free forging is 1140 to 1170°C, preferably 1140 to 1150°C.
  • the purpose of two piercing and one lengthening is to make the blank produce a larger amount of deformation, obtain smaller grains, and at the same time obtain uniform horizontal and vertical grain sizes, in preparation for die forging.
  • the bar material is directly machined into a rotor, and the bar material is not deformed and has no forging ratio.
  • the invention obtains a larger forging ratio of the bar through the forging method.
  • the free forging forging ratio is greater than 3, so that the crystal grains are violently deformed, and the accumulated energy will cause the boundary of the deformed crystal grains to form a new crystal grain nucleation core, and recrystallization occurs. , The formation of small and uniform equiaxed grains.
  • the final forging temperature is higher than 900°C.
  • the forging billet stack is cooled to 300°C and then air-cooled. The main purpose is to prevent excessive cooling speed from causing uneven thermal stress on the core and surface of the forging billet and cracks. After the blank is free forged, a forging blank is obtained.
  • Step 23 the first annealing treatment of the blank
  • the forging billet is put into a resistance furnace and the temperature is raised to 640-660°C, preferably 640-650°C, and the temperature is kept for 12-20h, preferably 12-15h.
  • the first annealing treatment is to eliminate the structural defects caused by uneven forging deformation, reduce the dislocation density between the grains of the forging, make the structure uniform, and eliminate residual stress.
  • the annealing temperature of the blank is 620 to 640°C, or without annealing treatment.
  • the annealing temperature range of the present invention is higher because the forging blank is in the free forging process.
  • the medium forging ratio is large, the deformation is large, and the internal stress is large. The internal stress can be eliminated through a higher annealing temperature.
  • Step 24 The billet is subjected to surface treatment after annealing treatment to obtain a forged billet.
  • the surface treatment of forgings uses a shot blasting machine to clean the surface oxide scale of the forging blanks after forging, and to polish the surface defects of the forgings.
  • the purpose of surface treatment is to prevent defects such as surface cracks from entering the interior of the part during the subsequent die forging process, or continue to crack to reduce the yield and affect the performance of the forging.
  • step 3 the specific steps are as follows:
  • Step 31 The forging blank is heated for the second time after the above-mentioned surface treatment
  • the second heating is to heat the surface-treated forging billet to prepare for die forging.
  • the gas furnace is heated to 750 ⁇ 780°C
  • the forging billet is loaded and kept for 1.5 ⁇ 3h, then the temperature is raised to 1120°C ⁇ 1150°C at a rate of 100 ⁇ 150°C/h, and the temperature is kept for 1 ⁇ 2h.
  • the temperature is increased to 1120°C to 1150°C at a rate of 100 to 150°C/h, and the preferred heating rate is 120 to 150°C/h, which can be used to forge the surface of the billet during the heating process.
  • the temperature to the core is more uniform and the temperature gradient is small.
  • the use of 1120°C ⁇ 1150°C and the holding time of 1 ⁇ 2h can reduce energy consumption. Secondly, it suppresses the growth of austenite grains at high temperatures and ensures the material structure. Uniformity.
  • the heating rate is different during the two heating processes.
  • the first heating is heating before free forging, and the heating rate is faster.
  • the second heating is for die forging. In order to have the same temperature inside and outside the forging blank, the heating rate is therefore slow.
  • the first time the heating rate is fast is to shorten the heating time. If the heating time is too long, the crystal grains will grow up.
  • the second reduction in heating rate is due to the fact that the heating rate is too fast, which will cause a large internal and external temperature gradient, resulting in thermal stress, deterioration of thermal plasticity, and affecting forging deformation.
  • Step 32 The forging blank is die forged after the second heating
  • the forging temperature for die forging of the forging blank is 1120 to 1140°C, and the preferred temperature for forging is 1120 to 1130°C.
  • the forging blank at this temperature has good thermoplasticity and is beneficial to deformation.
  • the final forging temperature of die forging is greater than 900°C. In order to avoid stress concentration at the edges and corners of the die forging process, the final forging temperature should be as high as possible, but at the same time, considering that the crystal grains are sufficiently broken and fine grains are obtained, the preferred final forging temperature is higher than 950 °C. After die forging, the forging is air-cooled to room temperature to obtain the forging.
  • the deformation method of the forging blank under the lower die is used, and the method of pressing and deforming is performed 5 times.
  • the forging blank after the second heating is placed in the cavity of the lower die of the die forging machine with a manipulator. Adjust the centering of the forging blank and the die axis to avoid eccentricity during the forging process.
  • For the first deformation use 2000-3000 tons of pressure to press the upper die to press the forging blank to ensure that the forging blank is centered and fixed in the cavity of the lower die.
  • the upper die is used to press the forging billet under a pressure of more than 5,000 tons, which can obtain a larger forging ratio and fully crush the grains.
  • the fourth deformation uses a pressure of 4500 tons to press the forging billet.
  • the forging blank can fill the cavity of the upper and lower dies.
  • the forging blank is pressed under a pressure of 4000 tons and held for 30-40 seconds.
  • the blank forging can further fill the cavity of the upper and lower dies, and the forging blank is in the cavity at the same time.
  • the internal holding for 30-40 seconds can release the stress at the edges and corners, and can make the internal and external temperature and structure of the forging billet more uniform, and can also ensure that the external dimensions meet the requirements.
  • the thickness direction of the forging blank is reduced from 280mm to 100 ⁇ 120mm, the forging ratio is greater than 2, and the cavity of the die is filled.
  • a forging with a shape similar to that of the high-speed rotor is obtained. Large deformation occurs in the horizontal and vertical directions, and the properties of the material tend to be consistent in all directions.
  • Step 33 Perform a second annealing process on the forging blank after die forging
  • the forgings after die forging into a resistance furnace heat up to 640°C ⁇ 660°C, keep for 25h ⁇ 30h, then cool to room temperature with the furnace in air, the preferred annealing temperature is 640 ⁇ 650°C, secondary annealing can eliminate the structure of die forgings Defects, once again reduce the density of dislocations between grains, homogenize the structure, and eliminate residual stress.
  • Step 34 The forging blank after die forging undergoes solution treatment after the second annealing process to obtain a forging.
  • the solution treatment dissolves alloying elements or precipitated phases into high-temperature austenite to prepare for the dispersion and precipitation of precipitated phases in the aging process, and can make the structure more uniform. Therefore, during solution treatment, the forging blank after die forging is heated in a resistance furnace to a solution temperature of 1035 ⁇ 1045°C, the preferred solution temperature is 1040°C, and the holding time is 1 to 1.5h. The preferred holding time is 1h.
  • the forging billet is air-cooled to below 32°C and air-cooled to below 32°C in order to complete the martensite transformation and ensure that the steel obtains higher strength.
  • step 4 the specific steps are as follows:
  • Step 41 Rough machining of the forging. Forgings, milling machines and lathes are used for rough machining of die forgings, leaving a finishing allowance of 1 ⁇ 1.5mm;
  • Step 42 The forging is subjected to aging treatment after rough machining.
  • the rough-processed forgings are heated to 550-560°C in a resistance furnace, kept for 4 to 4.5 hours, and air-cooled to room temperature.
  • the preferred temperature is 550°C
  • the preferred holding time is 4h.
  • Step 43 The forging is finally finished after finishing.
  • the machine tool is used to finish the aging forgings to meet the final surface quality and size requirements, and the final surface quality reaches Ra1.6.
  • the shape of the die forgings is a gyro shape, as shown in Figure 1.
  • This embodiment provides a high-strength stainless steel rotor whose element composition is calculated by mass percentage: C: 0.043%, Cr: 15.4%, Ni: 5.35%, Cu: 2.52%, Nb+Ta: 0.41%, Mo: 0.53 %, V: 0.08%, Si: 0.25%, Mn: 0.46%, P: 0.005%, S ⁇ 0.010%, O ⁇ 0.003%, and the rest are iron and inevitable impurity elements.
  • the present invention provides a method for preparing a high-strength stainless steel rotor, which includes the following steps:
  • Step 1 Prepare rotor stainless steel blank
  • Preparation size is The high-strength stainless steel billet, the surface burr is removed, and the end face is rounded R20.
  • Step 2 Free forging is performed on the blank after the first heating, and the first annealing and surface treatment are performed after the free forging to obtain a forging blank;
  • Step 21 The billet is heated for the first time in a gas furnace
  • the billet After the gas furnace is heated to 750°C, the billet is loaded and kept for 1.5 hours, and then the temperature is raised to 1140°C at a rate of 250°C/h, and the temperature is kept for 2.5 hours.
  • Step 22 Free forging of the blank
  • the billet into a 1000-ton fast forging machine first upset the billet to the diameter
  • the height is about 280mm, and then stretched to the diameter
  • the height is about 440mm, and then the second pier is thickened to the diameter
  • the height is 280mm
  • the forging temperature is 1140°C
  • the final forging temperature is 950°C.
  • the forging billet is pile-cooled to 300°C and then air-cooled.
  • the forging ratio is about 4.5.
  • Step 23 After the blank is free forged, the first annealing and surface treatment are performed to obtain a forging blank;
  • the billet After free forging, the billet is heated to 640°C in a resistance furnace for 12 hours, and the furnace is cooled to room temperature. Use a shot blasting machine to clean the surface oxide scale of the forged blank and polish the surface defects of the forging.
  • Step 3 The forging blank is heated for the second time, die forging is performed after the second heating, and the second annealing and solution treatment are performed after die forging to obtain a forging;
  • Step 31 the forging blank is heated for the second time
  • the forging billet is loaded and kept for 2 hours, then the temperature is raised to 1130°C at a rate of 150°C/h, and the temperature is kept for 1 hour.
  • Step 32 Perform die forging on the forging blank after the second heating
  • the forging billet after the second heating of the gas furnace is put into a 6000-ton die forging machine for die forging.
  • the first deformation uses 3000 tons of pressure to press the upper die to press the forging billet, and the forging billet is centered and merged.
  • the second and third deformations use 5300 tons of pressure to press the upper die to press the forging blanks
  • the fourth deformation uses 4500 tons of pressure to press the forging blanks to completely fill the upper and lower molds.
  • the blank was forged under a pressure of 4000 tons and held for 30 seconds.
  • the thickness direction of the forging blank is pressed down from 280mm to 105mm, so that the cavity of the upper and lower molds is filled.
  • the forging temperature is 1120°C and the final forging temperature is 950°C. After forging, it is air-cooled to room temperature.
  • Step 33 After die forging, the forging blank is annealed a second time;
  • Step 34 After the second annealing, the forging blank is solid-melted to obtain a forging;
  • the forging billet after the second annealing is heated to 1040°C in a resistance furnace, after holding for 1 hour, it is air-cooled to below 32°C.
  • Step 4 A high-strength stainless steel rotor is produced after rough machining, aging treatment and finishing of the forging.
  • Step 41 Rough machining of the forging
  • a milling machine and a lathe are used for rough machining of the die forgings, leaving a finishing allowance of 1mm.
  • Step 42 Aging treatment
  • Step 43 Finish machining of the forging after aging treatment
  • the machine tool is used to finish the aging forgings to meet the final surface quality and size requirements, and the final surface quality reaches Ra1.6.
  • the shape of the die forgings is a gyro shape, as shown in Figure 1.
  • the difference is that the open forging temperature in free forging is 1150°C, and the final forging temperature is 900°C. After forging, the forging billet is pile-cooled to 300°C and then air-cooled.
  • the mechanical properties are shown in Table 1.
  • the difference is: in the die forging process, the first deformation uses 3000 tons of pressure to press the upper die to press the forging blank, and the forging blank is centered and fixed in the cavity of the lower die.
  • the upper die is pressed down with a pressure of 5,500 tons
  • the fourth deformation is forged with a pressure of 4,500 tons, so that the forgings can completely fill the cavities of the upper and lower molds.
  • the fifth deformation is used
  • the forging billet is pressed under a pressure of 4000 tons and held for 40 seconds.
  • the thickness direction of the forging blank is pressed down from 280mm to 120mm, so that the cavity of the upper and lower molds is filled.
  • the forging temperature is 1140°C and the final forging temperature is 950°C. After forging, it is air-cooled to room temperature.
  • the mechanical properties are shown in Table 1.
  • the difference is that the forging blank after the second annealing treatment is heated to 1035° C. in a resistance furnace, and after holding for 1 hour, it is air-cooled to below 32° C.
  • the mechanical properties are shown in Table 1.
  • the difference is: the aging treatment is heated to 560°C, held for 4 hours, and cooled to room temperature in air.
  • the mechanical properties are shown in Table 1.
  • Example 1 The rotor preparation method described in Example 1 is adopted. The difference is that the thickness direction of the forging blank is reduced from 280 mm to 150 mm during the die forging process.
  • the mechanical properties are shown in Table 1.
  • the coarse and mixed crystals are shown in Fig. Particle size measurement method described in GB/T 6394.
  • Example 1 The rotor method described in Example 1 is used, but the difference is that after the aging treatment is heated to 540° C., the temperature is kept for 4 hours, and then air-cooled to room temperature.
  • the mechanical properties are shown in Table 1.
  • Table 1 lists the measured room temperature mechanical properties of the high-speed rotor, and the mechanical performance test is tested in accordance with the standard GB/T228.
  • the high-strength stainless steel rotor prepared by the present invention has excellent mechanical properties, its tensile strength R m is not less than 1100 MPa; the yield strength R p0.2 is not less than 1000 MPa; the elongation after fracture A is not low
  • the reduction of area Z is not less than 55%; the hardness is not less than 36HRC, the mechanical properties meet the standard requirements, and the difference between the horizontal and vertical properties is very small, which meets the design and use requirements.
  • Figures 3 and 4 are the austenite grain morphologies of the core and edges of the high-speed rotor prepared in Example 1.
  • the grain sizes of the two are similar.
  • the average grain size is between 6.5 and 7.0, and the high-speed rotor is at different positions.
  • the organization is almost the same, and the preparation method of the present invention can obtain a more uniform organization.
  • Figure 5 and Figure 6 are the austenite grain morphology of the core and edge of Comparative Example 1. Mixed crystals appeared due to poor control of the forging ratio, and the coarse grains were severe, the elongation decreased significantly, which did not meet the target The requirements have affected the performance of the rotor.
  • Comparative Example 2 the aging temperature was 540°C. After 4 hours of heat preservation, although the strength has been greatly improved, its elongation and reduction of area are significantly reduced, and the performance does not meet the index requirements, which affects the performance of the rotor.
  • the method for preparing a high-strength stainless steel high-speed rotor effectively combines free forging and die forging processes to increase the amount of deformation and forging ratio to obtain a high-speed rotor with uniform structure and stable performance.
  • the preparation method greatly reduces the processing volume, improves the utilization rate of raw materials, adopts a reasonable heat treatment process to control the organization, reduces the loss of processing tools, and all properties meet the index requirements, and the prepared high-speed rotor has a uniform structure, horizontal and vertical There is no obvious difference in mechanical properties, excellent performance, and meet the actual service requirements.

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Abstract

本发明涉及一种高强度不锈钢转子及其制备方法，属于金属材料热加工技术领域，解决了现有技术中转子强度低，服役寿命短以及锻造中切削工艺原料浪费多，成本高的问题。本发明首先准备转子不锈钢坯料，之后对转子不锈钢坯料进行第一次加热后进行自由锻，自由锻后进行第一次退火以及表面处理，制得锻坯；再进行第二次加热，第二次加热后进行模锻，模锻后进行第二次退火处理和固溶处理，制得锻件；最后对锻件经粗加工、时效处理以及精加工后制得高强度不锈钢转子。使用本发明制备方法得到了高强度、耐疲劳性能优良的转子，并降低了转子制备过程中的生产成本。

Description

一种高强度不锈钢转子及其制备方法
本申请要求于2020年4月29日提交中国专利局、申请号为202010357799.5、发明名称为“一种高强度不锈钢转子及其制备方法”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本发明涉及金属材料热加工技术领域，尤其涉及一种高强度不锈钢转子及其制备方法。
背景技术
高强度不锈钢具有高强韧性与耐蚀性能，是优良的结构材料，广泛应用于石油、化工、民船、航天、民机等领域。目前高强度不锈钢的锻件使用广泛，锻造工艺已有相关研究。
高速转子是陀螺仪中的重要部件，高强度不锈钢由于具有高强度、高韧性、高尺寸稳定性、耐蚀性等特点，因此用于制造高速转子可达到较好的服役性能。现有技术采用1Cr18Ni9Ti不锈钢，通过自由锻工艺制备棒料，再经过切削加工制备高速转子，切削加工量较大，极大的浪费了原材料，增加了成本。同时，通过棒材机加工的转子的金属流线是不封闭的，使用过程中存在安全隐患；另外，采用1Cr18Ni9Ti不锈钢材料制备的转子强度只有560MPa，强度较低导致其服役寿命短。
发明内容
鉴于上述的分析，本发明实施例旨在提供一种高强度不锈钢转子及其制备方法，用以解决现有技术中转子强度低，服役寿命短以及锻造中切削工艺原料浪费多，成本高的问题。
本发明是通过以下技术方案实现：
一种高强度不锈钢转子，转子的元素组成按质量百分比计为：C：0.03％～0.050％、Cr：14.90％～15.80％、Ni：5.00％～5.70％、Cu：2.20％～2.80％、Nb+Ta：0.35％～0.44％、Mo：0.45％～0.54％、V：0.06％～0.10％、Si：0.20％～0.60％、Mn：0.40％～0.80％、P≤0.010％、S≤0.010％、O≤0.003％，其余为铁和不可避免的杂质元素。
进一步，所述转子的元素组成按质量百分比计为：C：0.043％、Cr： 15.4％、Ni：5.35％、Cu：2.52％、Nb+Ta：0.41％、Mo：0.53％、V：0.08％、Si：0.25％、Mn：0.46％、P：0.005％、S≤0.010％，O≤0.003％，其余为铁和不可避免的杂质元素。
一种高强度不锈钢转子的制备方法，用于制备上述的高强度不锈钢转子，包括如下步骤：
步骤1：准备转子不锈钢坯料；
步骤2：所述转子不锈钢坯料进行第一次加热后进行自由锻，自由锻后进行第一次退火以及表面处理，制得锻坯；
步骤3：所述锻坯进行第二次加热，第二次加热后进行模锻，模锻后进行第二次退火处理和固溶处理，制得锻件；
步骤4：所述锻件经粗加工、时效处理以及精加工后制得高强度不锈钢转子。
进一步，所述步骤1中，转子不锈钢坯料的长度为450～480mm，直径为φ350mm。
进一步，所述步骤2中，第一次加热过程为：燃气炉升温至750℃，将坯料装入燃气炉，保温1.5～2h，随后以200～300℃/h的速率升温至1140～1170℃，保温2～3h。
进一步，所述步骤2中，自由锻包括转子不锈钢坯料的两次墩粗和一次拔长，一次镦粗至直径
Figure PCTCN2021090831-appb-000001
再拔长至直径
Figure PCTCN2021090831-appb-000002
二次墩粗至直径
Figure PCTCN2021090831-appb-000003
转子不锈钢坯料自由锻开锻温度1140～1170℃，终锻温度大于等于900℃，坯料自由锻后堆冷至300℃后散开，空冷至室温。
进一步，所述步骤2中，第一次退火处理为将自由锻后坯料放入电阻炉加热至640℃～660℃，保温12h～20h，随炉冷却至室温，制得锻坯。
进一步，所述步骤3中，第二次加热为：燃气炉升温至750℃，装入锻坯，保温1.5～3h，再以100～150℃/h的速率升温至1120℃～1150℃，保温1～2h。
进一步，所述步骤3中，模锻过程为：将第二次加热后的锻坯放入模锻机中进行模锻；模锻始锻温度为1120～1140℃，终锻温度大于等于900℃；模锻后锻坯空冷至室温。
进一步，所述模锻的过程中采用下模具下压锻件的变形方式，并进行5次下压变形；所述5次下压变形为：
第1次下压变形用2000～3000吨压力使上模具下压锻坯；
第2次和第3次下压变形用5000吨以上的压力使上模具下压锻坯；
第4次下压变形用4500吨压力下压锻坯；
第5次下压变形用4000吨压力下压锻坯，并保持30～40秒。
进一步，所述模锻后，所得锻坯的厚度方向由280mm下压至100～120mm，锻造比大于2。
进一步，所述步骤3中，第二次退火处理是将模锻后锻坯放入电阻炉中，升温至640℃～660℃，保温25h～30h，炉冷至室温。
进一步，所述步骤3中，固溶处理是将第二次退火处理的锻坯置于电阻炉中加热至1035～1045℃，保温1～1.5h，保温结束后锻坯空冷至32℃以下，制得锻件。
进一步，所述步骤4中，时效处理是将粗加工后的锻件放入电阻炉中加热至550～560℃，保温4～4.5h，空冷至室温。
进一步，所述精加工后所得高强度不锈钢转子的表面质量达到Ra1.6。
与现有技术相比，本发明至少可实现如下有益效果之一：
1、本发明采用高强度不锈钢材料，经自由锻与模锻两次锻造工艺的复合使用，以及自由锻与模锻之前分别进行加热与自由锻与模锻之后分别进行退火处理，在最后一次退火处理后，锻件又经过固溶处理、粗加工、时效处理、精加工处理后，转子的抗拉强度R m不低于1100MPa；屈服强度Rp 0.2不低于1000MPa；断后伸长率A不低于15％；断面收缩率Z不低于55％；硬度不低于36HRC，较现有的转子强度提高了500MPa以上，提高了转子的服役寿命。
2、本发明采用先自由锻后模锻的制备工艺，自由锻的锻造比大于3，模锻的锻造比大于2，自由锻和模锻的累计锻造比大于5，横向、纵向均有大的变形量，奥氏体晶粒度细小，晶粒得到较大的破碎，晶粒度细小(6级以上)，使得锻件横、纵向力学性能一致，提高了转子高速旋转部件的疲劳寿命，安全可靠性提高。
3、本发明中坯料自由锻包括两次墩粗和一次拔长过程。坯料第一次 镦粗至直径
Figure PCTCN2021090831-appb-000004
再拔长至直径
Figure PCTCN2021090831-appb-000005
第二次墩粗至直径
Figure PCTCN2021090831-appb-000006
坯料经过两次墩粗和一次拔长后开始进行自由锻。坯料自由锻的开锻温度1140～1170℃，优选为1140～1150℃。坯料自由锻中进行两次墩粗与一次拔长目的是使坯料产生较大的变形量，获得尺寸较小的晶粒，同时坯料获得横向和纵向晶粒大小均匀一致。
4、本发明中采用自由锻后第一次退火处理与模锻后经第二次退火处理，锻造过程中严格控制开锻和终锻的温度区间，自由锻开锻温度1140～1170℃，终锻温度大于900℃；模锻开锻温度为1120～1140℃，模锻终锻温度大于900℃，此温度下的锻坯热塑性好，控制每次的变形量和变形尺寸利于变形，保证了锻造过程材料的塑性，获得较大的锻造比，不出现裂纹等缺陷。
5、本发明中锻件经固溶处理后粗加工可以减小刀具损耗，并留有很小的精加工余量，在时效后再精加工，可以降低由于材料硬度增加而导致刀具的耗损量。
6、本发明中采用自由锻和模锻相结合的制备工艺，可以获得金属流线沿着锻件的外形呈封闭流线，制备的转子整体金属流线封闭，提高了锻件的抗疲劳性能和使用安全性，适合于10年以上周期服役。
7、本发明的锻件切削加工量小，节约了原料使用量，有效地降低了成本，避免了传统技术采用棒材直接切削加工成锻件形状，加工量大，原材料浪费的问题，且产品一致性好，合格率达到100％。
本发明中，上述各技术方案之间还可以相互组合，以实现更多的优选组合方案。本发明的其他特征和优点将在随后的说明书中阐述，并且，部分优点可从说明书中变得显而易见，或者通过实施本发明而了解。本发明的目的和其他优点可通过说明书以及附图中所特别指出的内容中来实现和获得。
附图说明
附图仅用于示出具体实施例的目的，而并不认为是对本发明的限制，在整个附图中，相同的参考符号表示相同的部件。
图1为转子模锻件示意图；
图2为转子示意图；
图3为实施例1中高速转子心部晶粒度；
图4为实施例1中高速转子边部晶粒度；
图5为对比例1中高速转子心部晶粒度；
图6为对比例1中高速转子边部晶粒度。
具体实施方式
下面结合附图来具体描述本发明的优选实施例，其中，附图构成本申请一部分，并与本发明的实施例一起用于阐释本发明的原理，并非用于限定本发明的范围。
本发明的一个具体实施例，公开了一种高强度不锈钢转子，其元素组成按质量百分比计为：C：0.03％～0.050％、Cr：14.90％～15.80％、Ni：5.00％～5.70％、Cu：2.20％～2.80％、Nb+Ta：0.35％～0.44％、Mo：0.45％～0.54％、V：0.06％～0.1％、Si：0.20％～0.60％、Mn：0.40％～0.80％、P≤0.010％、S≤0.010％、O≤0.003％，其余为铁和不可避免的杂质元素。
为了获得高强度的转子，加入了5.00～5.70％的Ni，获得马氏体组织；加入强化元素Cu(2.20～2.80％)，析出第二相ε-Cu；加入Nb，获得NbC析出相；Mo的加入起到了固溶强化作用。为了保证疲劳性能，P和S降低到0.01％以下；为了降低氧化物夹杂的含量，提高疲劳性能，O降低到0.003％以下；为了提高转子的耐腐蚀性，合金配比Cr元素为14.90～15.80％。
另一方面，本发明提供一种高强度不锈钢转子的制备方法，包括如下步骤：
步骤1：准备转子不锈钢坯料；
步骤2：坯料进行第一次加热后进行自由锻，自由锻后进行第一次退火以及表面处理，制得锻坯；
第一次加热过程为：燃气炉升温至750℃，将坯料装入燃气炉，保温1.5～2h，随后以200～300℃/h的速率升温至1140～1170℃，保温2～3h。自由锻包括坯料的两次墩粗和一次拔长，一次镦粗至直径
Figure PCTCN2021090831-appb-000007
再拔长至直径
Figure PCTCN2021090831-appb-000008
二次墩粗至直径
Figure PCTCN2021090831-appb-000009
坯料自由锻开锻温度1140～1170℃，终锻温度大于等于900℃，坯料锻后堆冷至300℃后散开，空冷至室温；第一次退火处理为将自由锻后坯料放入电阻炉加热 至640℃～660℃，保温12h～20h，随炉冷却至室温，制得锻坯。
步骤3：锻坯进行第二次加热，第二次加热后进行模锻，模锻后进行第二次退火处理和固溶处理，制得锻件；
第二次加热为：燃气炉升温至750℃，装入锻坯，保温1.5～3h，再以100～150℃/h的速率升温至1120℃～1150℃，保温1～2h。模锻过程为：将锻坯放入模锻机中进行模锻，始锻温度为1120～1140℃，终锻温度大于等于900℃，锻后锻坯空冷至室温。第二次退火处理是将模锻后锻坯放入电阻炉中，升温至640℃～660℃，保温25h～30h之后，炉冷至室温。固溶处理是将第二次退火处理后锻坯置于电阻炉中加热至1035～1045℃，保温1～1.5h，空冷至32℃以下，制得锻件。
步骤4：锻件经粗加工、时效处理以及精加工，制得高强度不锈钢转子；
时效处理是将粗加工后的锻件放入电阻炉中加热至550～560℃，保温4～4.5h，空冷至室温，制得转子。
具体的，步骤1中，准备尺寸为直径
Figure PCTCN2021090831-appb-000010
的高强度不锈钢棒材，锯切长度450～480mm的坯料，去除表面毛刺。为了缓和后续锻造过程中的棱角处应力集中，消除安全隐患，本发明在坯料的两个端面倒圆角R20。
步骤2中，具体步骤如下：
步骤21：坯料在燃气炉中进行第一次加热；
燃气炉升温至750～760℃后，装入坯料并保温1.5～2h，随后以200～300℃/h的速率升温至1140～1170℃，保温2～3h。选择将坯料在750～760℃装炉，使坯料快速通过400～470℃脆性温度区间，降低坯料的脆性。坯料在400～470℃温度区间长时间保温，组织中会析出强化相，增加材料受内热应力影响而产生裂纹倾向。
与现有技术中燃气炉的升温速率在100℃/h，本发明中坯料的升温速率为200～300℃/h的速率下快速升温至1140～1170℃，缩短升温耗费的时间，降低能源消耗，提高生产效率。同时，缩短升温速率还可以抑制不锈钢坯料在高温下奥氏体晶粒长大，提高坯料的强度，降低坯料的塑性；坯料在1140～1170℃保温2～3h，可以保证坯料锻造前温度和组织的均匀性。
步骤22：坯料自由锻；
坯料自由锻包括两次墩粗和一次拔长过程。坯料第一次镦粗至直径
Figure PCTCN2021090831-appb-000011
再拔长至直径
Figure PCTCN2021090831-appb-000012
第二次墩粗至直径
Figure PCTCN2021090831-appb-000013
坯料经过两次墩粗和一次拔长后开始进行自由锻。坯料自由锻的开锻温度1140～1170℃，优选为1140～1150℃。坯料自由锻中进行两次墩粗与一次拔长目的是使坯料产生较大的变形量，获得尺寸较小的晶粒，同时可获得横向和纵向晶粒大小均匀一致，为模锻做准备。
现有技术中棒材直接进行机械加工成转子，棒材不产生变形，也无锻造比例。本发明把棒材通过锻造方式获得较大的锻造比，自由锻锻造比大于3，使晶粒剧烈变形，积聚的能量会使变形晶粒的边界形成新的晶粒形核核心，发生再结晶，形成细小均匀的等轴晶粒。
另外，本发明为了保证坯料充分变形，使晶粒破碎细小，又不至坯料在锻造过程中开裂，因此终锻温度大于900℃。自由锻后将锻坯堆冷至300℃后散开空冷，其目的主要是为了防止冷速过快导致锻坯心部和表面产生热应力不均匀而出现裂纹。坯料经自由锻后制得锻坯。
步骤23：坯料第一次退火处理；
锻坯放入电阻炉中升温至640～660℃，优选640～650℃，保温12h～20h，优选12～15h。第一次退火处理是为了消除由于锻造变形不均匀产生的组织缺陷，降低锻件晶粒间的位错密度，使组织均匀化，消除残余应力。
现有技术中，坯料的退火温度为620～640℃，或者不退火处理，与现有技术中退火温度620～640℃相比，本发明的退火温度范围较高，是因为锻坯在自由锻中锻造比大，变形大，内应力大，通过更高的退火温度来消除内应力。
步骤24：坯料在经过退火处理后进行表面处理，制得锻坯。
锻件表面处理使用抛丸机清理锻后锻坯的表面氧化皮，并打磨锻件表面缺陷。表面处理的目的是防止表面裂纹等缺陷在后续模锻过程中进入部件内部，或继续开裂而降低成材率和影响锻件性能。
步骤3中，具体步骤如下：
步骤31：锻坯经上述表面处理后进行第二次加热；
第二次加热是将表面处理过的锻坯进行加热，为模锻做准备。燃气炉升温至750～780℃后，装入锻坯并保温1.5～3h，再以100～150℃/h的速率 升温至1120℃～1150℃，保温1～2h。将锻坯在750～780℃装炉，使锻坯加热温度快速通过400～470℃脆性温度区间，若在该温度区间长时间保温，组织中会析出沉淀强化相，极大的增加了材料由于受内热应力影响而产生裂纹倾向，以100～150℃/h的速率升温至1120℃～1150℃，优选的升温速率120～150℃/h，采用该升温速率可以在加热过程中锻坯的表面到心部的温度更加均匀，温度梯度小，采用1120℃～1150℃，保温时间1～2h，可以降低能源消耗，其次是抑制了高温下奥氏体晶粒长大，且保证了材料组织的均匀性。
特别的，本发明中两次加热过程中的升温速率不同，第一次加热是自由锻之前加热，加热速率较快，第二次加热是为了模锻，为了锻坯内外温度一致，因此加热速率慢。另外，第一次升温速率快是为了缩短加热时间，加热时间过长会发生晶粒的长大。第二次加热速率降低是由于加热速度过快会造成内外温度梯度大，形成热应力，热塑性变差，影响锻造变形。
步骤32：锻坯在第二次加热后进行模锻；
锻坯模锻开锻温度为1120～1140℃，优选的开锻温度为1120～1130℃，此温度下的锻坯热塑性好，利于变形。模锻终锻温度大于900℃，为避免模锻过程棱角处发生应力集中，终锻温度尽量高，但同时考虑晶粒得到充分破碎并获得细小的晶粒，故优选的终锻温度高于950℃。模锻后锻件空冷至室温，制得锻件。
模锻过程中采用下模具下压锻坯的变形方式，并进行5次下压变形的方式，首先用机械手将第二次加热后的锻坯放置在模锻机的下模具的型腔内，调整锻坯的轴心与模具轴心对中，避免锻造过程中发生偏心，第1次变形用2000～3000吨压力使上模具下压锻坯，保证锻坯对中并固定在下模具的型腔中，第2次和第3次变形用5000吨以上的压力使上模具下压锻坯，可获得较大的锻造比，充分破碎晶粒，第4次变形用4500吨压力下压锻坯，可使锻坯填满上下模具的型腔，第5次变形用4000吨压力下压锻坯，并保持30～40秒，可使锻坯进一步填满上下模具型腔，同时锻坯在型腔内保持30～40秒可以使棱角处的应力得到释放，并可以使锻坯内外温度和组织更加均匀，也可以保证外形尺寸达到要求。经过模锻后，锻坯的厚度方向由280mm下压至100～120mm，锻造比大于2，填满模具 的型腔，通过模锻获得形状与高速转子近似的锻件，后续加工量少，保证了横纵向均发生较大的变形，材料各方向上性能趋于一致。
步骤33：模锻后的锻坯进行第二次退火过程；
将模锻后的锻件放入电阻炉中，升温至640℃～660℃，保温25h～30h，之后随炉空冷至室温，优选退火温度为640～650℃，二次退火可以消除模锻件的组织缺陷，再次降低晶粒间的位错密度，使组织均匀化，并消除残余应力。
步骤34：模锻后的锻坯经第二次退火过程后进行固溶处理，制得锻件。
固溶处理将合金元素或析出相固溶于高温奥氏体中，为时效过程中的析出相弥散析出做准备，并可以使组织更加均匀。因此，固溶处理时将模锻后的锻坯在电阻炉中加热至固溶温度1035～1045℃，优选的固溶温度为1040℃，保温1～1.5h，优选的保温时间1h，之后将锻坯空冷至32℃以下，空冷至32℃以下是为了使马氏体相变完全，保证钢获得较高的强度。
步骤4中，具体步骤如下：
步骤41：锻件进行粗加工。锻件采用铣床和车床对模锻件进行粗加工，留下1～1.5mm的精加工余量；
步骤42：锻件经粗加工后进行时效处理。将粗加工后的锻件在电阻炉中加热至550～560℃后，保温4～4.5h，空冷至室温。其中，优选的温度为550℃，优选的保温时间是4h。通过时效处理可以在钢中析出大量的富Cu和Nb(CN)等细小、弥散的强化相，大幅度提高钢的强度，满足力学性能使用要求；
步骤43：锻件最后经精加工后成材。采用机床对时效后的锻件进行精加工，达到最终表面质量与尺寸要求，达到最终表面质量达到Ra1.6，模锻件外形是陀螺形状，如图1所示。
实施例1
本实施例提供一种高强度不锈钢转子，其元素组成按质量百分比计为：C：0.043％、Cr：15.4％、Ni：5.35％、Cu：2.52％、Nb+Ta：0.41％、Mo：0.53％、V：0.08％、Si：0.25％、Mn：0.46％、P：0.005％、S≤0.010％，O≤0.003％，其余为铁和不可避免的杂质元素。
另一方面，本发明提供一种高强度不锈钢转子的制备方法，包括如下步骤：
步骤1：准备转子不锈钢坯料；
准备尺寸为
Figure PCTCN2021090831-appb-000014
的高强度不锈钢坯料，去除表面毛刺，并在端面倒圆角R20。
步骤2：坯料进行第一次加热后进行自由锻，自由锻后进行第一次退火以及表面处理，制得锻坯；
步骤21：坯料在燃气炉中第一次加热；
燃气炉升温至750℃后，装入坯料并保温1.5h，后以250℃/h的速率升温至1140℃，保温2.5h。
步骤22：坯料进行自由锻；
将坯料放入1000吨快锻机中，首先进行一次镦粗，将坯料墩粗至直径
Figure PCTCN2021090831-appb-000015
高度约280mm，再拔长至直径
Figure PCTCN2021090831-appb-000016
高度约440mm，再进行二次墩粗至直径
Figure PCTCN2021090831-appb-000017
高度280mm，开锻温度1140℃，终锻温度为950℃，锻后将锻坯堆冷至300℃后散开空冷，锻造比约为4.5。
步骤23：坯料自由锻后进行第一次退火及表面处理后，制得锻坯；
自由锻后坯料放入电阻炉中加热至640℃，保温12h，炉冷至室温。使用抛丸机清理锻后坯料表面氧化皮，并打磨锻件表面缺陷。
步骤3：锻坯进行第二次加热，第二次加热后进行模锻，模锻后进行第二次退火和固溶处理，制得锻件；
步骤31：锻坯进行第二次加热；
燃气炉升温至750℃后，装入锻坯并保温2h后，以150℃/h的速率升温至1130℃，保温1h。
步骤32：第二次加热后锻坯进行模锻；
将燃气炉二次加热后的锻坯放入6000吨模锻机中进行模锻，模锻过程中，第1次变形用3000吨压力使上模具下压锻坯，并使锻坯对中并固定在下模具的型腔中，第2次和第3次变形用5300吨的压力使上模具下压锻坯，第4次变形用4500吨压力下压锻坯，使锻坯完全填满上下模具的型腔，第5次变形用4000吨压力下压锻坯，并保持30秒。锻坯厚度方向由280mm下压至105mm，使得填满上下模具的型腔，开锻温度为 1120℃，终锻温度为950℃，锻后空冷至室温。
步骤33：模锻后锻坯进行第二次退火；
将模锻后的锻坯放入电阻炉中加热至640℃，保温25h后，炉冷至室温。
步骤34：第二次退火后锻坯进行固熔处理，制得锻件；
将第二次退火后锻坯在电阻炉中加热至1040℃，保温1h后，空冷至32℃以下。
步骤4：锻件经粗加工、时效处理以及精加工后制得高强度的不锈钢转子。
步骤41：锻件粗加工；
采用铣床和车床对模锻件进行粗加工，留下1mm的精加工余量。
步骤42：时效处理；
将粗加工的锻件放入电阻炉中加热至550℃，保温4h后，空冷至室温。
步骤43：时效处理后锻件精加工；
采用机床对时效后的锻件进行精加工，达到最终表面质量与尺寸要求，达到最终表面质量达到Ra1.6，模锻件外形是陀螺形状，如图1所示。
实施例2
根据实施例1所述的方法，不同的是：自由锻中开锻温度1150℃，终锻温度为900℃，锻后将锻坯堆冷至300℃后散开空冷，力学性能见表1。
实施例3
根据实施例1所述的方法，不同的是：模锻过程中，第1次变形用3000吨压力使上模具下压锻坯，并使锻坯对中并固定在下模具的型腔中，第2次和第3次变形用5500吨的压力使上模具下压锻坯，第4次变形用4500吨压力下压锻坯，使锻坯完全填满上下模具的型腔，第5次变形用4000吨压力下压锻坯，并保持40秒。锻坯厚度方向由280mm下压至120mm，使得填满上下模具的型腔，开锻温度为1140℃，终锻温度为950℃，锻后空冷至室温，力学性能见表1。
实施例4
根据实施例1所述的方法，不同的是：将第二次退火处理后的锻坯在电阻炉中加热至1035℃，保温1h之后，空冷至32℃以下，力学性能见表1。
实施例5
根据实施例1所述的方法，不同的是：时效处理为加热至560℃后，保温4h，空冷至室温，力学性能见表1。
对比例1
采用实施例1所述转子的制备方法，不同的是：模锻过程中锻坯厚度方向由280mm下压至150mm，力学性能见表1，粗晶和混晶如图5所示，金属平均晶粒度测定法GB/T 6394中记载的方法进行测量的。
对比例2
采用实施例1所述的转子的方法，不同的是：时效处理时加热至540℃后，保温4h，空冷至室温，力学性能见表1。
表1列出高速转子的实测室温力学性能，力学性能试验按照标准GB/T228测试。
表1实施例1～5与对比例1～2中转子室温力学性能与晶粒粒度结果
Figure PCTCN2021090831-appb-000018
Figure PCTCN2021090831-appb-000019
由表1可以看出，采用本发明制备的高强度不锈钢转子的力学性能优异，其抗拉强度R m不低于1100MPa；屈服强度R p0.2不低于1000MPa；断后伸长率A不低于15％；断面收缩率Z不低于55％；硬度不低于36HRC，力学性达到标准要求，且横向、纵向性能差异极小，满足设计使用要求。
图3与图4分别是实施例1制备的高速转子心部与边部的奥氏体晶粒形貌，两者晶粒尺寸近似，平均晶粒度在6.5级～7.0级，高速转子不同位置的组织是近乎一致的，本发明制备方法可获得更加均匀的组织。
图5和图6分别是对比例1的心部与边部的奥氏体晶粒形貌，由于锻造比控制不佳出现了混晶，且粗晶严重，伸长率下降明显，不满足指标要求，影响了转子的性能。
对比例2中时效温度采用540℃，保温4h后，虽然强度有了较大的提升，但其伸长率和断面收缩率显著的下降，性能不满足指标要求，影响了转子的性能。
综上所述，本发明提供的高强度不锈钢高速转子的制备方法通过将自由锻与模锻工艺有效的结合起来，增加的变形量和锻造比，获得组织均匀、性能稳定的高速转子，本发明制备方法大大的降低了加工量，提高了原材料的利用率，采用合理的热处理工艺调控组织，减少了加工刀具的损耗，各项性能均达到指标要求，且制备出的高速转子组织均匀、横纵向力学性能无明显差异，性能优异，满足实际服役要求。
以上所述，仅为本发明较佳的具体实施方式，但本发明的保护范围并不局限于此，任何熟悉本技术领域的技术人员在本发明揭露的技术范围内，可轻易想到的变化或替换，都应涵盖在本发明的保护范围之内。

Claims (15)

  1. 一种高强度不锈钢转子，其特征在于，转子的元素组成按质量百分比计为：C：0.03％～0.050％、Cr：14.90％～15.80％、Ni：5.00％～5.70％、Cu：2.20％～2.80％、Nb+Ta：0.35％～0.44％、Mo：0.45％～0.54％、V：0.06％～0.10％、Si：0.20％～0.60％、Mn：0.40％～0.80％、P≤0.010％、S≤0.010％、O≤0.003％，其余为铁和不可避免的杂质元素。
  2. 根据权利要求1所述的高强度不锈钢转子，其特征在于，所述转子的元素组成按质量百分比计为：C：0.043％、Cr：15.4％、Ni：5.35％、Cu：2.52％、Nb+Ta：0.41％、Mo：0.53％、V：0.08％、Si：0.25％、Mn：0.46％、P：0.005％、S≤0.010％，O≤0.003％，其余为铁和不可避免的杂质元素。
  3. 一种高强度不锈钢转子的制备方法，用于制备权利要求1或2所述的高强度不锈钢转子，其特征在于，包括如下步骤：
    步骤1：准备转子不锈钢坯料；
    步骤2：所述转子不锈钢坯料进行第一次加热后进行自由锻，自由锻后进行第一次退火以及表面处理，制得锻坯；
    步骤3：所述锻坯进行第二次加热，第二次加热后进行模锻，模锻后进行第二次退火处理和固溶处理，制得锻件；
    步骤4：所述锻件经粗加工、时效处理以及精加工后制得高强度不锈钢转子。
  4. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤1中，转子不锈钢坯料的长度为450～480mm，直径为
    Figure PCTCN2021090831-appb-100001
  5. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤2中，第一次加热过程为：燃气炉升温至750℃，将转子不锈钢坯料装入燃气炉，保温1.5～2h，随后以200～300℃/h的速率升温至1140～1170℃，保温2～3h。
  6. 根据权利要求3或4所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤2中，自由锻包括转子不锈钢坯料的两次墩粗和一次拔长，一次镦粗至直径
    Figure PCTCN2021090831-appb-100002
    再拔长至直径
    Figure PCTCN2021090831-appb-100003
    二次墩粗至 直径
    Figure PCTCN2021090831-appb-100004
    转子不锈钢坯料自由锻的开锻温度1140～1170℃，终锻温度大于等于900℃，转子不锈钢坯料自由锻后堆冷至300℃后散开，空冷至室温。
  7. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤2中，第一次退火处理为将自由锻后坯料放入电阻炉加热至640℃～660℃，保温12h～20h，随炉冷却至室温。
  8. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤3中，第二次加热为：燃气炉升温至750℃，装入锻坯，保温1.5～3h，再以100～150℃/h的速率升温至1120℃～1150℃，保温1～2h。
  9. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤3中，模锻过程为：将第二次加热后的锻坯放入模锻机中进行模锻；模锻始锻温度为1120～1140℃，终锻温度大于等于900℃；模锻后锻坯空冷至室温。
  10. 根据权利要求3或9所述的高强度不锈钢转子的制备方法，其特征在于，所述模锻的过程中采用下模具下压锻件的变形方式，并进行5次下压变形；所述5次下压变形为：
    第1次下压变形用2000～3000吨压力使上模具下压锻坯；
    第2次和第3次下压变形用5000吨以上的压力使上模具下压锻坯；
    第4次下压变形用4500吨压力下压锻坯；
    第5次下压变形用4000吨压力下压锻坯，并保持30～40秒。
  11. 根据权利要求10所述的高强度不锈钢转子的制备方法，其特征在于，所述模锻后，所得锻坯的厚度方向由280mm下压至100～120mm，锻造比大于2。
  12. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤3中，第二次退火处理是将模锻后锻坯放入电阻炉中，升温至640℃～660℃，保温25h～30h，炉冷至室温。
  13. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤3中，固溶处理是将第二次退火处理的锻坯置于电阻炉中加热至1035～1045℃，保温1～1.5h，保温结束后锻坯空冷至32℃以下，制得锻件。
  14. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述步骤4中，时效处理是将粗加工后的锻件放入电阻炉中加热至550～560℃，保温4～4.5h，空冷至室温。
  15. 根据权利要求3所述的高强度不锈钢转子的制备方法，其特征在于，所述精加工后所得高强度不锈钢转子的表面质量达到Ra1.6。
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