CN116288071B - Low-temperature hot-set precipitation-hardening austenitic stainless steel and preparation method and application thereof - Google Patents
Low-temperature hot-set precipitation-hardening austenitic stainless steel and preparation method and application thereof Download PDFInfo
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 33
- 238000004881 precipitation hardening Methods 0.000 title claims abstract description 24
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 40
- 239000000956 alloy Substances 0.000 claims abstract description 40
- 239000013078 crystal Substances 0.000 claims abstract description 22
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 9
- 239000010935 stainless steel Substances 0.000 claims abstract description 9
- 238000007711 solidification Methods 0.000 claims abstract description 4
- 230000008023 solidification Effects 0.000 claims abstract description 4
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 30
- 238000001816 cooling Methods 0.000 claims description 23
- 238000009792 diffusion process Methods 0.000 claims description 22
- 238000009826 distribution Methods 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 17
- 239000011159 matrix material Substances 0.000 claims description 16
- 229910052786 argon Inorganic materials 0.000 claims description 15
- 229910052802 copper Inorganic materials 0.000 claims description 13
- 239000010949 copper Substances 0.000 claims description 13
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 11
- 229910052804 chromium Inorganic materials 0.000 claims description 11
- 239000011651 chromium Substances 0.000 claims description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 11
- 238000010273 cold forging Methods 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 10
- 239000011572 manganese Substances 0.000 claims description 10
- 230000006698 induction Effects 0.000 claims description 9
- 238000010587 phase diagram Methods 0.000 claims description 9
- 239000000126 substance Substances 0.000 claims description 9
- 229910052720 vanadium Inorganic materials 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 8
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 6
- 229910001309 Ferromolybdenum Inorganic materials 0.000 claims description 6
- MBMLMWLHJBBADN-UHFFFAOYSA-N Ferrous sulfide Chemical compound [Fe]=S MBMLMWLHJBBADN-UHFFFAOYSA-N 0.000 claims description 6
- 229910000628 Ferrovanadium Inorganic materials 0.000 claims description 6
- 235000010627 Phaseolus vulgaris Nutrition 0.000 claims description 6
- 244000046052 Phaseolus vulgaris Species 0.000 claims description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 6
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- 210000000795 conjunctiva Anatomy 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 239000002994 raw material Substances 0.000 claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 241001062472 Stokellia anisodon Species 0.000 claims description 2
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 238000002844 melting Methods 0.000 claims description 2
- 230000008018 melting Effects 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 31
- 239000006104 solid solution Substances 0.000 abstract description 5
- 238000005728 strengthening Methods 0.000 abstract description 5
- 238000005204 segregation Methods 0.000 abstract description 4
- 125000004429 atom Chemical group 0.000 abstract description 3
- 230000007246 mechanism Effects 0.000 abstract description 3
- 125000004434 sulfur atom Chemical group 0.000 abstract description 3
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- 230000009471 action Effects 0.000 abstract description 2
- 239000002131 composite material Substances 0.000 abstract description 2
- 238000006073 displacement reaction Methods 0.000 abstract description 2
- 239000000243 solution Substances 0.000 description 20
- 229910001566 austenite Inorganic materials 0.000 description 13
- 238000001556 precipitation Methods 0.000 description 13
- 239000000203 mixture Substances 0.000 description 12
- 239000002244 precipitate Substances 0.000 description 11
- 238000000034 method Methods 0.000 description 8
- 238000005242 forging Methods 0.000 description 7
- 238000003723 Smelting Methods 0.000 description 6
- 229910000905 alloy phase Inorganic materials 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 238000011068 loading method Methods 0.000 description 5
- 238000003825 pressing Methods 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 238000004088 simulation Methods 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 238000000227 grinding Methods 0.000 description 3
- 239000000155 melt Substances 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 210000001787 dendrite Anatomy 0.000 description 2
- 238000011049 filling Methods 0.000 description 2
- 238000009434 installation Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
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- 238000006731 degradation reaction Methods 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
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- 230000003647 oxidation Effects 0.000 description 1
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- 230000002035 prolonged effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
Classifications
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- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23Q—DETAILS, COMPONENTS, OR ACCESSORIES FOR MACHINE TOOLS, e.g. ARRANGEMENTS FOR COPYING OR CONTROLLING; MACHINE TOOLS IN GENERAL CHARACTERISED BY THE CONSTRUCTION OF PARTICULAR DETAILS OR COMPONENTS; COMBINATIONS OR ASSOCIATIONS OF METAL-WORKING MACHINES, NOT DIRECTED TO A PARTICULAR RESULT
- B23Q3/00—Devices holding, supporting, or positioning work or tools, of a kind normally removable from the machine
- B23Q3/12—Devices holding, supporting, or positioning work or tools, of a kind normally removable from the machine for securing to a spindle in general
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- 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
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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- 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
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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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- Crystallography & Structural Chemistry (AREA)
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- Heat Treatment Of Steel (AREA)
Abstract
The invention belongs to the technical field of stainless steel materials, and relates to low-temperature hot-set precipitation-hardening austenitic stainless steel, and a preparation method and application thereof. According to the invention, the atomic distance is increased by adding alloy elements with different proportions, the alloy elements adopt a gap or displacement solid solution mode, the atomic lattice volume of a face-centered cubic structure is enlarged, the thermal expansion coefficient of the material at low temperature and normal temperature is improved, the composite solid solution strengthening is carried out under the combined action of a plurality of alloy elements, the high-temperature stability of the material is improved, the interatomic bonding capacity and the uniform distribution of atoms are improved through directional solidification and intervention of a deformation mechanism, the crystal orientation and a bent grain boundary are controlled, the segregation of sulfur atoms and alloy elements in the grain boundary is controlled by adopting amplitude modulation treatment, the grain boundary is purified, the performance of the grain boundary is improved, and the material is strengthened.
Description
Technical Field
The invention belongs to the technical field of stainless steel materials, and relates to low-temperature hot-set precipitation-hardening austenitic stainless steel, and a preparation method and application thereof.
Background
The thermal shrinkage type knife handle adopts stainless steel or die steel as a knife handle thermal expansion sleeve material, hard alloy is used as a knife tool holding material, the difference of thermal expansion coefficients of the two materials is utilized, the knife tool handle is heated in a short time through a thermal induction device, after the inner diameter of the thermal expansion sleeve is enlarged, the knife tool is loaded into the knife tool handle, when the thermal expansion sleeve of the knife tool handle is cooled and contracted, uniform clamping force is generated, the clamping force between the knife tool and the knife handle is uniform, the structure is compact and symmetrical, the high-performance thermal expansion knife handle material is utilized, the hard alloy knife is clamped by utilizing the thermal expansion and contraction principle, the knife tool is enabled to jump less, the important problems of balance, jump precision, clamping strength and the like in high-speed processing can be solved, and the service life of the knife tool can be prolonged by more than 30% through high-precision installation.
The high-performance thermal expansion knife handle material is required to have the following properties: ① The high thermal expansion coefficient can realize 300-DEG C low-temperature hot loading and heat extraction, ② high mechanical properties, high precision and high rigidity clamping force and the service life of the cutter and the main shaft.
At present, research and development of stainless steel knife handle materials for low-temperature hot-filling and stainless steel knife handle materials in China basically belongs to the blank, the stainless steel knife handle materials are not specially used for knife handle materials, most of domestic factories select die steel or austenitic stainless steel as knife handle hot-expansion sleeves, the thermal expansion coefficient is small, high-temperature oxidation generally occurs when the knife handle is hot-filled at the temperature of more than 400 ℃, the heat intensity and the heat stability are poor, the low-temperature hot-filling at the temperature of below 300 ℃ cannot be realized, the overall hardness after heat treatment is low, the clamping degree is required to be adjusted, the high-precision installation cannot be realized, the precision degradation can occur after the knife handle is hot-filled for more than 800 times, and the service life is low.
Disclosure of Invention
The present invention has been made in view of the above problems occurring in the prior art, and an object of the present invention is to provide a low-temperature hot-set precipitation-hardening austenitic stainless steel which has high heat stability and does not undergo a change in precision when subjected to heat loading and unloading several thousands of times or more.
The aim of the invention can be achieved by the following technical scheme: a low-temperature hot-set precipitation-hardening austenitic stainless steel comprises ：0.55-0.65％ C,0.3-0.4％ Si,10-11％ Cr,6.5-7.5％ Mn,7.5-8.5％Ni,2.0-2.5％ Mo,0.1-0.15％ S,2.0-3.0％ Al,1.0-2.0％ V,2.0-3.0％Cu, parts by mass of raw materials of a stainless steel knife handle and the balance of Fe.
In the low-temperature hot-set precipitation-hardening austenitic stainless steel, the hardness of the stainless steel is HRC 44-46, and the thermal expansion coefficient at 300-400 ℃ is (17-19) multiplied by 10 -6K-1.
The invention also provides a preparation method of the low-temperature hot-set precipitation hardening austenitic stainless steel, which comprises the following steps:
s1, firstly placing pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium and pure copper in an induction furnace to smelt to obtain a pre-alloy;
S2, after prealloying and melting the conjunctiva, sequentially adding carbon powder, metallic aluminum beans, electrolytic manganese and ferrous sulfide for smelting to form a uniform alloy solution, and then pouring the alloy solution into a water-cooling copper mold to obtain an ingot;
S3, after the ingot is fully directionally solidified and cooled, determining precipitated phases in an austenitic matrix at different temperatures of alloy elements and equilibrium distribution in the crystal grain and near a crystal boundary by adopting phase diagram analysis software according to the chemical components actually measured;
s4, performing diffusion treatment after solidification of the cast ingot, and then performing cold forging to obtain a bar;
s5, sequentially carrying out solution treatment and amplitude modulation treatment on the bar.
Preferably, the smelting temperature in the step S1 is 1600-1700 ℃.
Preferably, the smelting temperature in the step S2 is 1650-1700 ℃.
In the above-mentioned preparation method of low-temperature hot-set precipitation-hardening austenitic stainless steel, the diffusion treatment in step S4 specifically includes: preserving the temperature for 1-3h at 1150-1120 ℃, and then cooling along with the furnace.
Preferably, the diffusion treatment temperature is 1180 ℃.
The invention adopts a diffusion treatment process to reduce or eliminate the chemical components and microstructure (dendrite) segregation of the alloy steel, thereby achieving the purpose of homogenization; meanwhile, the diffusion treatment can destroy disordered growth of an as-cast dendrite structure, reduce element diffusion barriers, and enable alloy elements to be distributed uniformly and carbide to be distributed more uniformly; after the casting is subjected to diffusion treatment, cold deformation treatment can be directly carried out. The diffusion treatment of the invention is generally heated slightly below the solidus temperature, i.e. 1150-1200 ℃, and in order to further avoid excessive growth of grains, the diffusion treatment temperature is controlled at 1180 ℃.
In the above method for preparing a low-temperature hot-set precipitation-hardening austenitic stainless steel, the cold forging reduction in step S4 is 30% → 10% → 10% → 10%. The invention adopts a cold forging forming process after diffusion treatment to obtain the required bar size. The deformation of the first pass is 30%, and under the condition of low temperature and large deformation, the dislocation density is increased by the larger deformation, so that the recrystallization driving force is improved, grains are refined, and the material performance is improved; due to the non-uniformity of large deformation of the first pass, crystallization nucleation is non-uniform, light-pressing slow forging is adopted in the subsequent preparation process to ensure that the grain size is uniform and fine, the rolling reduction of the second pass, the third pass, the fourth pass and the fifth pass is 10%, deformation resistance can be generated after the pass deformation interval, and the forging cracking risk can be increased by adopting large-size rolling reduction. Therefore, the cold forging forming process can obtain uniform and fine grain structure, can not crack in the forging process, improves the interatomic bonding capability and the uniform distribution of atoms through intervening a deformation mechanism, and controls the crystal orientation and bends grain boundaries.
In the preparation method of the low-temperature hot-set precipitation-hardening austenitic stainless steel, the solution treatment temperature in the step S5 is 1100-1200 ℃ and the time is 45min.
In the preparation method of the low-temperature hot-set precipitation-hardening austenitic stainless steel, the amplitude modulation treatment temperature in the step S5 is 750-780 ℃ and the time is 5-10h.
In the preparation method of the low-temperature hot-charging and precipitation hardening austenitic stainless steel, the amplitude modulation treatment adopts argon pressurizing sectional cooling control, the temperature interval of the first section is 300-780 ℃, the argon pressure is 9-10MPa, and the cooling speed is 100-130 ℃/min; the second stage has a temperature of 50-300 deg.C, argon pressure of 6-7MPa and cooling rate of 20-30 deg.C/min. The room temperature structure after solution treatment is austenite, and a large amount of alloy elements are dissolved in the austenite structure. By controlling the cooling process, the segregation of sulfur atoms and alloy elements in the grain boundary is controlled, the grain boundary is purified, the performance of the grain boundary is improved, and the material is reinforced.
The application of the low-temperature hot-set precipitation-hardening austenitic stainless steel in the thermal expansion sleeve of the thermal shrinkage type knife handle.
A thermal expansion sleeve of a thermal shrinkage type knife handle is prepared from the low-temperature hot-set precipitation hardening austenitic stainless steel.
Compared with the prior art, the invention has the following beneficial effects:
1. According to the invention, the atomic distance is increased by adding alloy elements with different proportions, the alloy elements adopt a gap or displacement solid solution mode, the atomic lattice volume of a face-centered cubic structure is enlarged, the thermal expansion coefficient of the material at low temperature and normal temperature is improved, the composite solid solution strengthening is carried out under the combined action of a plurality of alloy elements, the high-temperature stability of the material is improved, the interatomic bonding capacity and the uniform distribution of atoms are improved through directional solidification and intervention of a deformation mechanism, the crystal orientation and a bent grain boundary are controlled, the segregation of sulfur atoms and alloy elements in the grain boundary is controlled by adopting amplitude modulation treatment, the grain boundary is purified, the performance of the grain boundary is improved, and the material is strengthened.
2. According to the invention, by using a computer simulation means, the precipitation phases of alloy elements in an austenitic matrix at different temperatures and the balanced distribution of the inside of crystal grains and the vicinity of crystal boundaries are analyzed, and the technological parameters such as solid solution, deformation, amplitude modulation treatment and the like are accurately adjusted based on the distribution change conditions of the alloy elements in the inside of the crystal grains and the vicinity of the crystal boundaries, so that the hardness of the prepared precipitation hardening austenitic stainless steel can be accurately controlled between HRC44 and 46.
3. The precipitation hardening austenitic stainless steel prepared by the invention can reach a thermal expansion coefficient of 17-19 multiplied by 10 -6K-1 at a heating temperature of 300-400 ℃, has a heat-resistant temperature of not lower than 750 ℃, has high thermal stability, can not change precision when the knife handle is subjected to heat loading and unloading for thousands of times, and can be used as a low-temperature heat loading and knife handle thermal expansion sleeve material.
Drawings
FIG. 1 is a schematic view of a heat-shrinkable tool shank product;
FIG. 2 is a simulation result of the simulation analysis of the material prepared in example 1;
FIG. 3 is a grain size fraction of the material prepared in example 1;
FIG. 4 shows the microstructure morphology of the material prepared in example 2 (grain size grade in FIG. 4a, secondary electron image in crystal orientation in FIG. 4b, back scattered electron image in crystal orientation in FIG. 4c, precipitate morphology in FIG. 4 d);
FIG. 5 is the elemental distribution (FIG. 5a elemental distribution surface scan position, FIG. 5b elemental XRD analysis) within the matrix of the material prepared in example 3;
fig. 6 shows the morphology and composition of the grain boundary precipitates (fig. 6a for grain boundary precipitates and fig. 6b for grain boundary precipitates) of the material prepared in example 3.
Detailed Description
The following are specific examples of the present invention, and the technical solutions of the present invention are further described, but the present invention is not limited to these examples.
Example 1:
s1, preparing the following raw materials in percentage by mass:
C:0.578%, si:0.33%, cr:10.47%, mn:6.6%, ni:7.62%, mo:2.1%, S:0.107%, al:2.1%, V:1.2%, cu:2.08%, fe: the balance;
s2, firstly, placing pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium and pure copper into an induction furnace, sequentially starting a mechanical pump and a diffusion pump for vacuumizing, and smelting at 1650 ℃;
S3, after prealloy melts the conjunctiva, the induction furnace is powered off, air is filled in to open a furnace cover, carbon powder, metallic aluminum beans, electrolytic manganese and ferrous sulfide are sequentially added, the two alloys are smelted at 1680 ℃, and through observation of a visual window, after each component is uniformly dissolved into an alloy solution, the alloy solution is poured into a water-cooled copper mold to obtain an ingot;
S4, after the ingot is fully directionally solidified and cooled, determining precipitated phases in an austenitic matrix at different temperatures of alloy elements by adopting phase diagram analysis software according to the chemical components actually measured, wherein simulation analysis phase diagram simulation results are shown in FIG. 2, and equilibrium distribution inside crystal grains and near crystal boundaries is shown in Table 1;
Table 1: precipitation of phases in austenitic matrix at different temperatures
S5, after the ingot is fully directionally solidified and cooled, performing diffusion treatment, and heating at the temperature: 1180 ℃ and the heat preservation time is 2 hours, and the furnace is cooled. The cold deformation strengthening phase transformation is adopted, the cast ingot after the diffusion treatment is forged into a bar, the cold forging reduction is 30% -10%, the follow-up pass can adopt light pressing, rapid forging is carried out, and the pass interval time is 60S.
S6, carrying out solution treatment and amplitude modulation treatment on the finished bar, carrying out solution treatment at 1100 ℃, preserving heat for 45 minutes, and carrying out water cooling; amplitude modulation processing: preserving heat for 8 hours at 750 ℃, adopting argon pressurizing sectional cooling control, wherein the cooling speed is 120 ℃/min, and the argon pressure is 9-10MPa in the temperature range of 750-300 ℃; the temperature range is 300-50 ℃, the argon pressure is 6-7Mpa, and the cooling speed is high: 25 ℃/min.
According to the actual chemical composition, the phase diagram analysis software is used for determining the precipitation phases of alloy elements in an austenite matrix at different temperatures and the equilibrium distribution of the inside of grains and the vicinity of grain boundaries, and the equilibrium distribution is shown in figure 1.
And (3) grinding and polishing the sample to prepare a standard metallographic sample, and observing and photographing the standard metallographic sample by using a Germany ZEISS imager.A2m metallographic microscope in an etched state. The microstructure of the sample is austenite, the grain size is 7 grades, and the morphology is shown in figure 3. A schematic of the heat-shrinkable handle product is shown in fig. 1.
Table 2: example 1 Low temperature hot-set, precipitation-hardenable Austenitic stainless Steel Properties
Table 3: example 1 alloy phase composition and precipitation temperature of rod
| Alloy phase composition | Precipitation temperature/. Degree.C |
| (Mo, V, cr) 2 C phase | 970-975 |
| (Cr, mo) 23C6 phase | 930-935 |
| (V,Mo)C | 880-885 |
| Ferrite body | 650-655 |
| (Cu,Mn) | 640-645 |
| Fe,Ni,Mn | 640-645 |
Example 2:
s1, preparing the following raw materials in percentage by mass:
C:0.61%, si:0.348%, cr:10.47%, mn:6.96%, ni:7.92%, mo:2.26%, S:0.126%, al:2.51%, V:1.492%, cu:2.48%, fe: the balance;
s2, firstly, placing pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium and pure copper into an induction furnace, sequentially starting a mechanical pump and a diffusion pump for vacuumizing, and smelting at 1650 ℃;
S3, after prealloy melts the conjunctiva, the induction furnace is powered off, air is filled in to open a furnace cover, carbon powder, metallic aluminum beans, electrolytic manganese and ferrous sulfide are sequentially added, the two alloys are smelted at 1680 ℃, and through observation of a visual window, after each component is uniformly dissolved into an alloy solution, the alloy solution is poured into a water-cooled copper mold to obtain an ingot;
S4, after the ingot is fully directionally solidified and cooled, determining precipitated phases in an austenitic matrix at different temperatures of alloy elements by adopting phase diagram analysis software according to the chemical components actually measured, wherein the equilibrium distribution of the inside of crystal grains and the vicinity of crystal boundaries is shown in the table 1;
table 4: EXAMPLE 2 precipitation of phases in Austenitic matrix at different temperatures
S5, after the ingot is fully directionally solidified and cooled, performing diffusion treatment, and heating at the temperature: 1180 ℃ and the heat preservation time is 2 hours, and the furnace is cooled. The cold deformation strengthening phase transformation is adopted, the cast ingot after the diffusion treatment is forged into a bar, the cold forging reduction is 30% -10%, the follow-up pass can adopt light pressing, rapid forging is carried out, and the pass interval time is 60S.
S6, carrying out solution treatment and amplitude modulation treatment on the finished bar, carrying out solution treatment at 1160 ℃, preserving heat for 45 minutes, and carrying out water cooling; amplitude modulation processing: maintaining the temperature at 760 ℃ for 8 hours, adopting argon pressurizing sectional cooling control, wherein the cooling speed is 120 ℃/min, and the argon pressure is 9-10 MPa in the temperature range of 760-300 ℃; the temperature range is 300-50 ℃, the argon pressure is 6-7 Mpa, and the cooling speed is high: 25 ℃/min.
According to the actual chemical composition, the phase diagram analysis software is used for determining the precipitation phases of alloy elements in an austenite matrix at different temperatures and the equilibrium distribution of the inside of grains and the vicinity of grain boundaries, and the equilibrium distribution is shown in figure 1.
And (3) grinding and polishing the sample to prepare a standard metallographic sample, and observing and photographing the standard metallographic sample by using a Germany ZEISS imager.A2m metallographic microscope in an etched state. The microstructure of the sample is austenite, the grain size is 7 grades, and the morphology is shown in figure 3.
Table 5: example 2 Low temperature hot-set, precipitation hardening austenitic stainless steel properties
Table 6: example 2 alloy phase composition and precipitation temperature of rod
| Alloy phase composition | Precipitation temperature/. Degree.C |
| (Mo, V, cr) 2 C phase | 970-975 |
| (Cr, mo) 23C6 phase | 930-935 |
| (V,Mo)C | 880-885 |
| Ferrite body | 650-655 |
| (Cu,Mn) | 640-645 |
| Fe,Ni,Mn | 640-645 |
Example 3:
s1, preparing the following raw materials in percentage by mass:
C:0.645%, si:0.396%, cr:10.986%, mn:7.46%, ni:8.48%, mo:2.42%, S:0.147%, al:2.91%, V:1.962%, cu:2.88%, fe: the balance;
s2, firstly, placing pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium and pure copper into an induction furnace, sequentially starting a mechanical pump and a diffusion pump for vacuumizing, and smelting at 1650 ℃;
S3, after prealloy melts the conjunctiva, the induction furnace is powered off, air is filled in to open a furnace cover, carbon powder, metallic aluminum beans, electrolytic manganese and ferrous sulfide are sequentially added, the two alloys are smelted at 1680 ℃, and through observation of a visual window, after each component is uniformly dissolved into an alloy solution, the alloy solution is poured into a water-cooled copper mold to obtain an ingot;
S4, after the ingot is fully directionally solidified and cooled, determining precipitated phases in an austenitic matrix at different temperatures of alloy elements by adopting phase diagram analysis software according to the chemical components actually measured, wherein the equilibrium distribution of the inside of crystal grains and the vicinity of crystal boundaries is shown in the table 1;
table 7: precipitation of phases in austenitic matrix at different temperatures
S5, after the ingot is fully directionally solidified and cooled, performing diffusion treatment, and heating at the temperature: 1180 ℃ and the heat preservation time is 2 hours, and the furnace is cooled. The cold deformation strengthening phase transformation is adopted, the cast ingot after the diffusion treatment is forged into a bar, the cold forging reduction is 30% -10%, the follow-up pass can adopt light pressing, rapid forging is carried out, and the pass interval time is 60S.
S6, carrying out solution treatment and amplitude modulation treatment on the finished bar, carrying out solution treatment at 1100 ℃, preserving heat for 45 minutes, and carrying out water cooling; amplitude modulation processing: preserving heat for 8 hours at 750 ℃, adopting argon pressurizing sectional cooling control, wherein the cooling speed is 120 ℃/min, and the argon pressure is 9-10MPa in the temperature range of 750-300 ℃; the temperature range is 300-50 ℃, the argon pressure is 6-7Mpa, and the cooling speed is high: 25 ℃/min.
According to the actual chemical composition, the phase diagram analysis software is used for determining the precipitation phases of alloy elements in an austenite matrix at different temperatures and the equilibrium distribution of the inside of grains and the vicinity of grain boundaries, and the equilibrium distribution is shown in figure 1.
And (3) grinding and polishing the sample to prepare a standard metallographic sample, and observing and photographing the standard metallographic sample by using a Germany ZEISS imager.A2m metallographic microscope in an etched state. The microstructure of the sample is austenite, the grain size is 7 grades, and the morphology is shown in figure 3.
Table 8: example 3 Low temperature hot-set, precipitation hardening austenitic stainless steel properties
Table 9: example 3 alloy phase composition and precipitation temperature of rod
| Alloy phase composition | Precipitation temperature/. Degree.C |
| (Mo, V, cr) 2 C phase | 970-975 |
| (Cr, mo) 23C6 phase | 930-935 |
| (V,Mo)C | 880-885 |
| Ferrite body | 650-655 |
| (Cu,Mn) | 640-645 |
| Fe,Ni,Mn | 640-645 |
Example 4:
The difference from example 1 is only that in step S1, pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium, pure copper and carbon powder, metallic aluminum beans, electrolytic manganese, ferrous sulfide are smelted together.
Example 5:
the difference from example 1 is only that the diffusion treatment of step S5 is not performed.
Example 6:
The difference from example 1 is only that the cold forging reduction in step S5 is 40% →20%.
Example 7:
The difference from example 1 is only that the step S6 amplitude modulation process is not performed.
Table 10: results of the bar Performance test of examples 1-7
FIG. 3 is a grain size fraction of the material prepared in example 1; from the figure, the microstructure of the sample is austenite, the crystal grains are fine and uniformly distributed, and the grain size is grade 7.
FIG. 4 shows the microstructure morphology of the material prepared in example 2 (grain size grade in FIG. 4a, secondary electron image in crystal orientation in FIG. 4b, back scattered electron image in crystal orientation in FIG. 4c, precipitate morphology in FIG. 4 d); as is clear from the figure, the matrix structure is austenite and grain boundary precipitates, the austenite grains are fine and uniformly distributed, the austenite grains have obvious orientation along the forging direction, and the precipitates are precipitated in grain boundaries in a granular and orderly manner.
FIG. 5 is the elemental distribution (FIG. 5a elemental distribution surface scan position, FIG. 5b elemental XRD analysis) within the matrix of the material prepared in example 3; from the figure, it is apparent that the alloy elements are fully dissolved in the austenite structure, and the alloy elements are uniformly distributed in the matrix.
FIG. 6 shows the morphology and composition of the grain boundary precipitates (FIG. 6a morphology of grain boundary precipitates, FIG. 6b elemental composition of grain boundary precipitates) of the material prepared in example 3; as can be seen from the figure, the grain boundary precipitates are composed of C, mn, cr, cu, mo, V, ni elements.
In conclusion, the precipitation hardening austenitic stainless steel prepared by the method can reach a thermal expansion coefficient of 17-19 multiplied by 10 -6K-1 at a heating temperature of 300-400 ℃, the heat-resistant temperature of the material is not lower than 750 ℃, the thermal stability is high, the precision of the thermal loading and unloading of the knife handle for thousands of times can not be changed, and the precipitation hardening austenitic stainless steel can be used as a low-temperature hot-charging and knife handle thermal expansion sleeve material.
The point values in the technical scope of the present invention are not exhaustive, and the new technical solutions formed by equivalent substitution of single or multiple technical features in the technical solutions of the embodiments are also within the scope of the present invention; meanwhile, in all the listed or unrecited embodiments of the present invention, each parameter in the same embodiment represents only one example of the technical scheme (i.e. a feasibility scheme), and no strict coordination and limitation relation exists between each parameter, wherein each parameter can be replaced with each other without violating axiom and the requirement of the present invention, except what is specifically stated.
The technical means disclosed by the scheme of the invention is not limited to the technical means disclosed by the technical means, and also comprises the technical scheme formed by any combination of the technical features. While the foregoing is directed to embodiments of the present invention, it will be appreciated by those skilled in the art that changes and modifications may be made without departing from the principles of the invention, and such changes and modifications are intended to be included within the scope of the invention.
The specific embodiments described herein are offered by way of example only to illustrate the spirit of the invention. Those skilled in the art may make various modifications or additions to the described embodiments or substitutions thereof without departing from the spirit of the invention or exceeding the scope of the invention as defined in the accompanying claims.
Claims (8)
1. The low-temperature hot-set precipitation-hardening austenitic stainless steel is characterized in that the austenitic stainless steel comprises the following raw materials in percentage by mass, and the balance of Fe is ：0.55-0.65% C, 0.3-0.4% Si,10-11% Cr,6.5-7.5% Mn,7.5-8.5% Ni,2.0-2.5% Mo,0.1-0.15% S,2.0-3.0% Al,1.0-2.0% V,2.0-3.0% Cu,; the preparation method of the austenitic stainless steel comprises the following steps:
s1, firstly placing pure iron, ferrovanadium, ferromolybdenum, metallic nickel, metallic silicon, metallic chromium and pure copper in an induction furnace to smelt to obtain a pre-alloy;
s2, after prealloying and melting the conjunctiva, sequentially adding carbon powder, metallic aluminum beans, electrolytic manganese and ferrous sulfide to form a uniform alloy solution, and then pouring the alloy solution into a water-cooling copper mold to obtain an ingot;
S3, after the ingot is fully directionally solidified and cooled, determining precipitated phases in an austenitic matrix at different temperatures of alloy elements and equilibrium distribution in the crystal grain and near a crystal boundary by adopting phase diagram analysis software according to the chemical components actually measured;
s4, performing diffusion treatment after solidification of the cast ingot, and then performing cold forging to obtain a bar;
S5, sequentially carrying out solution treatment and amplitude modulation treatment on the bar;
the cold forging reduction is 30% -10% in step S4.
2. The low temperature hot-set, precipitation-hardenable austenitic stainless steel of claim 1, wherein the stainless steel has a hardness of HRC 44-46 and a linear expansion coefficient of (17-19) x 10 -6 K-1 at 300-400 ℃.
3. The low-temperature hot-set, precipitation-hardenable austenitic stainless steel of claim 1, wherein the step S4 diffusion treatment is specifically: preserving the temperature for 1-3h at 1150-1120 ℃, and then cooling along with the furnace.
4. The low temperature hot-set, precipitation-hardenable austenitic stainless steel of claim 1, wherein the solution treatment temperature in step S5 is 1100-1200 ℃ for 45min.
5. The low temperature hot-set, precipitation-hardenable austenitic stainless steel of claim 1, wherein the amplitude modulation treatment in step S5 is performed at a temperature of 50-780 ℃ for a time of 5-10 hours.
6. The low-temperature hot-set and precipitation-hardening austenitic stainless steel according to claim 1, wherein the amplitude modulation treatment is controlled by argon pressurizing sectional cooling, the first temperature range is 300-780 ℃, the argon pressure is 9-10MPa, and the cooling speed is 100-130 ℃/min; the second stage has a temperature of 50-300 deg.C, argon pressure of 6-7MPa and cooling rate of 20-30 deg.C/min.
7. Use of the low temperature hot-set, precipitation-hardenable austenitic stainless steel of claim 1 in a hot-expansion sleeve of a heat-shrinkable tool shank.
8. A thermal expansion sleeve of a thermal shrinkage tool handle, which is characterized in that the thermal expansion sleeve is made of the low-temperature hot-set precipitation hardening austenitic stainless steel according to claim 1.
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