CN114457284A - High-silicon stainless steel material containing vanadium and titanium and preparation method thereof - Google Patents

High-silicon stainless steel material containing vanadium and titanium and preparation method thereof Download PDF

Info

Publication number
CN114457284A
CN114457284A CN202111070811.5A CN202111070811A CN114457284A CN 114457284 A CN114457284 A CN 114457284A CN 202111070811 A CN202111070811 A CN 202111070811A CN 114457284 A CN114457284 A CN 114457284A
Authority
CN
China
Prior art keywords
stainless steel
titanium
tempering
steel material
quenching
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN202111070811.5A
Other languages
Chinese (zh)
Other versions
CN114457284B (en
Inventor
潘鹏
陈蕴博
李积回
李有维
左玲立
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Yangjiang Shibazi Group Co ltd
Beijing National Innovation Institute of Lightweight Ltd
Original Assignee
Yangjiang Shibazi Group Co ltd
Beijing National Innovation Institute of Lightweight Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Yangjiang Shibazi Group Co ltd, Beijing National Innovation Institute of Lightweight Ltd filed Critical Yangjiang Shibazi Group Co ltd
Priority to CN202111070811.5A priority Critical patent/CN114457284B/en
Publication of CN114457284A publication Critical patent/CN114457284A/en
Application granted granted Critical
Publication of CN114457284B publication Critical patent/CN114457284B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/006—Making ferrous alloys compositions used for making ferrous alloys
    • 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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/008—Martensite

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention discloses a high-silicon stainless steel material containing vanadium and titanium and a preparation method thereof, belongs to the technical field of stainless steel materials, and solves the problem that the toughness and the wear resistance of the existing stainless steel cannot meet the requirements. The high-silicon vanadium-titanium-containing stainless steel comprises the following components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0. -0.20%, V: 0-0.20 percent of Fe, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities. The preparation method comprises the following steps: smelting molten steel, and then casting to obtain a cast ingot; forging the cast ingot to obtain a steel billet; the billet is annealed, quenched and tempered or the billet is annealed, austempered and tempered. Compared with 40Cr13 stainless steel, the high-silicon stainless steel material containing vanadium and titanium of the invention has the advantages that the tensile strength is improved by 30-34%, the elongation is improved by 1-1.5 times, and the hardness is improved by more than 18-22%.

Description

High-silicon stainless steel material containing vanadium and titanium and preparation method thereof
Technical Field
The invention belongs to the technical field of stainless steel materials, and particularly relates to high-silicon stainless steel containing vanadium and titanium and a preparation method thereof.
Background
At present, stainless steel materials in China are complete. Stainless steel is classified into five major series, i.e., ferritic stainless steel, martensitic stainless steel, austenitic stainless steel, ferritic-austenitic duplex stainless steel, and precipitation hardening stainless steel, according to the difference of the room temperature structure. The Cr13 type stainless steel has the comprehensive properties of good hardenability, higher hardness and wear resistance, good corrosion resistance and the like, is widely applied to parts such as cutters, turbine blades, bearings, valve ports, structural members, wear-resistant members and the like which have low requirements on corrosion resistance but have high requirements on mechanical properties, and is widely applied to various cutter materials due to the good wear resistance of the 40Cr13 stainless steel.
However, the insufficient toughness of the 40Cr13 martensitic stainless steel is a fatal weakness which is difficult to overcome, the prior heat treatment process of the Cr13 type only remains in the traditional heat treatment mode of quenching and tempering, and the bottleneck is met in the aspect of improving the comprehensive mechanical property of the stainless steel. Therefore, how to obtain high-toughness and high-wear-resistance 40Cr13 stainless steel becomes a problem to be solved by the technical personnel in the field.
Disclosure of Invention
In view of the above analysis, the present invention aims to provide a high-silicon vanadium-and titanium-containing stainless steel material and a preparation method thereof, and particularly to a high-silicon vanadium-and titanium-containing stainless steel material for knife scissors and a preparation method thereof, so as to solve the problem that the toughness and the wear resistance of stainless steel cannot meet the existing requirements, and particularly the problem that the toughness and the wear resistance of stainless steel for knife scissors cannot meet the existing requirements.
The purpose of the invention is mainly realized by the following technical scheme:
on one hand, the invention provides a high-silicon stainless steel material containing vanadium and titanium, which comprises the following components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0-0.20%, V: 0-0.20 percent of Ti and V, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities, wherein at least one of Ti and V is added in the required content range.
Further, the stainless steel material comprises the following components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0.10% -0.20%, V: 0.10 to 0.20 percent of the total weight of the alloy, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities.
On the other hand, the invention provides a preparation method of a high-silicon stainless steel material containing vanadium and titanium, which comprises the following steps:
step S1, smelting molten steel, and then casting to obtain a cast ingot;
step S2, forging the cast ingot to obtain a steel billet;
and step S3, carrying out spheroidizing annealing treatment on the billet to obtain an annealed billet.
And step S4, quenching and tempering the annealed steel billet to obtain a final steel billet, wherein the quenching and tempering are oil quenching and secondary tempering or isothermal quenching and tempering.
Further, the step S1 includes: and (2) putting the scrap steel, pig iron, ferrochrome and nickel blocks into an induction smelting furnace, after molten steel is dissolved, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device for vacuum smelting, raising the highest temperature of the molten steel to 1550-.
Further, the step S2 includes: heating the ingot obtained in the step S1 to 1150-1180 ℃, preserving heat for 1-2h for homogenization, then forging, wherein the initial forging temperature is 1050-1100 ℃, the final forging temperature is 850-900 ℃, three-dun three-drawing is adopted in the forging process, and the billet obtained after forging is air-cooled to room temperature.
Further, the step S3 includes: putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800-850 ℃, preserving heat, and then heating to 860-880 ℃ for heat preservation; then cooling to 730-750 deg.C, heat-insulating, cooling to 550-600 deg.C, finally taking out and air-cooling to room temperature.
Further, in the step S4, the quenching and tempering treatment is oil quenching and secondary tempering;
the quenching comprises the following steps: placing the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800-; aging at room temperature for 1-2h, and then carrying out secondary tempering;
the secondary tempering comprises: reheating to 250-450 ℃, preserving heat for 1.8-2.2h, and then air-cooling to room temperature; then heating to 250-450 deg.C, heat-insulating for 1.8-2.2h, then air-cooling again to room temperature.
Further, after oil quenching and secondary tempering treatment, the microstructure is tempered martensite and retained austenite.
Further, in step S4, the quenching and tempering treatment is austempering and tempering;
the quenching comprises the following steps: placing the steel billet obtained in the step S3 into a heat treatment furnace, heating to 800-;
the tempering comprises: reheating to 250-450 ℃, preserving heat for 2h, and then air cooling to room temperature.
Further, after isothermal quenching and tempering treatment, the microstructure is bainite.
Compared with the prior art, the invention has the following beneficial effects:
1. according to the invention, the content of Si is controlled to be 1.00-2.00%, the function of cementite precipitation is inhibited, supersaturated carbon in martensite can be diffused into austenite, the stability of austenite is improved, more film-shaped residual austenite can be obtained after cooling to room temperature, and the plasticity and toughness of the material can be effectively improved. In addition, Si shifts the bainite transformation region in the CCT curve to the lower right, so that bainite transformation occurs at a lower temperature, fine needle-shaped bainite can be formed, bainite can be formed in a larger temperature range, and a uniform bainite structure can be obtained.
2. The invention utilizes the combined action of Mn and Si to obtain high strength and high hardness, and simultaneously has higher toughness. When a proper amount of Mn is enriched at the phase boundary at the medium temperature, the Mn plays a dragging role in phase boundary migration, and simultaneously, the phase transformation driving force of bainite is remarkably reduced, so that the phase transformation temperature of the bainite is reduced, and the bainite structure is favorably refined.
3. The invention controls the Ti content within 0.20%, preferably 0.10% -0.20%, and Ti generates TiC precipitation in the matrix, thus improving the recrystallization temperature of the material, pinning the prior austenite grains, hindering the growth of the austenite grains in the material and refining the martensite of the final matrix structure of the material.
4. The content of V is controlled within 0.20%, preferably 0.10% -0.20%, V and C form high-melting-point carbide VC which can be used as external crystal nucleus to refine crystal grains and improve the strength and toughness, and the hardness of the carbide is greater than that of M3C type carbide, so that the wear resistance of the material is improved.
5. According to the preparation method of the stainless steel material, provided by the invention, the microstructure of the stainless steel material is tempered martensite, residual austenite or bainite through accurately controlling the process steps and process parameters, and on the premise of ensuring the hardness requirement of the material, the microstructure of the stainless steel material is tempered martensite, residual austenite or bainiteV, Ti trace alloy element and high Si element are added, and forging and heat treatment processes are combined to control the dispersion precipitation of small-ball MC type carbide and inhibit M3The C-type carbide is precipitated, so that the grain size is 1/2 of 40Cr13 stainless steel, the impact toughness of the material is improved and increased, and compared with 40Cr13 stainless steel, the high-silicon vanadium and titanium-containing stainless steel material has the advantages that the tensile strength is improved by more than 30%, the elongation is improved by more than 1 time, and the hardness is improved by about 20%.
Drawings
FIG. 1 is a metallographic structure image in example 1 of the present invention;
FIG. 2 is a SEM image of a microstructure in example 1 of the present invention;
FIG. 3 is a metallographic structure image in example 2 of the present invention;
FIG. 4 is a SEM image of the microstructure in example 2 of the present invention;
FIG. 5 is a metallographic structure image obtained in example 3 of the present invention;
FIG. 6 is a SEM image of the microstructure in example 3 of the present invention.
FIG. 7 is a metallographic structure image obtained in example 4 of the present invention;
FIG. 8 is a SEM image of the microstructure in example 4 of the present invention;
FIG. 9 is a metallographic structure image obtained in example 5 of the present invention;
FIG. 10 is a SEM image of the microstructure in example 5 of the present invention;
FIG. 11 is a metallographic structure image obtained in example 6 of the present invention;
FIG. 12 is a SEM image of the microstructure in example 6 of the present invention.
Fig. 13 is a grain size micrograph of comparative material 40Cr 13.
Fig. 14 is a grain size microscopic image in example 1 of the present invention.
Fig. 15 is a grain size microscopic image in example 4 of the present invention.
Detailed Description
The following is a detailed description of a high-silicon vanadium-titanium-containing stainless steel and a method for making the same, which are given by way of illustration only and are not intended to limit the present invention.
The application provides a high-silicon stainless steel containing vanadium and titanium, which comprises the following chemical components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0-0.20%, V: 0-0.20 percent of Ti and V, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities, wherein at least one of Ti and V is added in the required content range.
The invention relates to a component design of high-silicon vanadium-titanium-containing stainless steel, which is based on the following principle:
carbon (C) element: the carbon content in the steel is improved, and more carbon can be distributed in the matrix through solid solution or in a mode of forming dispersed carbide, so that the effects of solid solution strengthening and dispersion strengthening are achieved. In general, the carbon content is increased, and the yield strength and tensile strength of the steel are increased, so that higher strength is provided, and fatigue crack initiation is prevented. Meanwhile, the plasticity of the steel increases with the increase of the carbon content, and when the carbon content is high to a certain degree, the fatigue property of the steel is reduced. Carbon is a strong interstitial solid solution strengthening element that increases strength, but cannot be relied upon to increase strength because high carbon content reduces impact toughness. Comprehensively considering, the content of C is controlled to be 0.35-0.40%.
Silicon (Si) element: silicon is an element which is very effective for replacing and solid solution strengthening ferrite, and Si is an effective element for improving tempering resistance, so that the tempering stability of steel can be improved. Si also plays a role in inhibiting cementite precipitation, so that supersaturated carbon in martensite can be diffused into austenite, the stability of the austenite is improved, more film-shaped residual austenite can be obtained after the martensite is cooled to room temperature, and the plasticity and toughness of the material can be effectively improved. In addition, Si shifts the bainite transformation region in the CCT curve to the lower right, so that bainite transformation occurs at a lower temperature, fine needle-shaped bainite can be formed, bainite can be formed in a larger temperature range, a uniform bainite structure can be obtained, and the air-cooling hardenability of the steel is improved. Therefore, the content of Si is controlled to be 1.00-2.00% by comprehensive consideration.
Manganese (Mn) element: manganese is a weak carbide forming element, generally exists in cementite in the form of carbide, and plays a good role in solid solution strengthening. When the Mn is in a certain content, the obvious upper and lower C curves on the supercooling austenite isothermal transformation curve are separated, when a proper amount of Mn is enriched at a phase boundary at a medium temperature, the dragging effect on the phase boundary migration is realized, the phase transformation driving force of the bainite is obviously reduced, the phase transformation temperature of the bainite is reduced, the bainite structure is favorably refined, and meanwhile, the bainite hardenability can be improved by the Mn. The Mn and Si act together to obtain high strength and high hardness, and simultaneously still have higher toughness. However, the Mn content in the steel should not be too high, so that the occurrence of remarkable temper brittleness due to the increase of the Mn content is avoided. Therefore, the Mn content is comprehensively considered to be controlled to be 0.60-1.00%.
Chromium (Cr) element: chromium can significantly improve the strength, hardness and wear resistance of the material, improve the oxidation resistance and corrosion resistance of the steel, and simultaneously reduce the plasticity and toughness. In an oxidizing medium, dense Cr can be generated on the metal surface along with the increase of the content of the chromium element2O3And the oxide film plays a strong role in passivation. The Cr element is a alloy element with the strongest ratio of reduction delta Bs/delta Ms, namely the Bs point and the Ms point, and can improve the strength of bainite. Furthermore, with increasing Cr content, the tendency to precipitate intermetallic compounds in stainless steels is increasing, the presence of these intermetallic compounds significantly reducing the plasticity and toughness of the steel and in some cases also impairing the corrosion resistance of the steel. Therefore, the content of Cr element is comprehensively considered to be controlled to be 10.00-13.00 percent.
Nickel (Ni) element: the addition of Ni not only affects the phase transformation process of the steel, but also affects the structure and the performance of the steel, and the Ni can simultaneously improve the strength and the toughness of the steel. After the Ni is added, the phase change of high-temperature ferrite is effectively hindered, Ms of experimental steel is reduced, and the phase change interval of bainite is expanded. When Ni is present, the plasticity and toughness properties can be improved, but the Ni content is controlled to be 0.20-0.60% in the invention because nickel is a rare metal and is relatively expensive.
Titanium (Ti) element: the microalloying element titanium (Ti) can react with carbon element in steel to generate TiC precipitate in a matrix, and TiC particles can influence the recrystallization of the material and improve the recrystallization temperature of the material; and the prior austenite grains can be pinned, the growth of the austenite grains in the material is hindered, and the martensite of the final matrix structure of the material is refined, so that the performance of the material is improved, but the hardness of the steel is reduced along with the increase of the Ti content. In addition, since TiC is very stable, the solid solution concentration of carbon in the alloy solid solution is also reduced. Therefore, the content of Ti is controlled within 0.20 percent.
Vanadium (V) element: v can refine crystal grains and improve the strength and toughness, V and C form high-melting-point carbide VC which can be used as external crystal nucleus to refine the crystal grains and improve the strength and toughness, and the hardness of the V is more than M3The C-type carbide is beneficial to improving the wear resistance of the material. The invention controls the content of V within 0.20%.
In order to further improve the performance of the high-silicon vanadium-and titanium-containing stainless steel, the composition of the high-silicon vanadium-and titanium-containing stainless steel can be further adjusted. Illustratively, the composition comprises, in mass percent: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0.10% -0.20%, V: 0.10 to 0.20 percent of the total weight of the alloy, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities.
The application also provides a preparation method of the high-silicon stainless steel material containing vanadium and titanium, which comprises the following steps:
step S1, smelting molten steel, and then casting to obtain a cast ingot;
specifically, step S1 includes: waste steel, pig iron, ferrochrome and nickel blocks are put into an induction smelting furnace, ferrosilicon, ferromanganese, titanium wires and ferrovanadium are sequentially added through a secondary feeding device for vacuum smelting after molten steel is dissolved, the highest temperature of the molten steel is raised to 1550-; obtaining the cast ingot with the diameter of 70-90 mm.
Step S2, forging the cast ingot to obtain a steel billet;
specifically, step S2 includes: heating the ingot obtained in the step S1 to 1150-1180 ℃, preserving heat for 1-2h for homogenization, then forging, wherein the initial forging temperature is 1050-1100 ℃, the final forging temperature is 850-900 ℃, three piers and three drawing are adopted in the forging process, and a billet with the diameter of 45-50mm is obtained after forging, and air cooling is carried out to the room temperature;
in the step 2, the homogenization treatment is to remove or reduce micro segregation in the steel ingot, homogenize chemical components, diffuse impurity distribution, improve plasticity of steel, and facilitate compaction, welding and repair of porosity defects in the steel ingot in the forging process.
Three piers and three pulls: upsetting the whole steel ingot to 1/3-1/2 of the height of the steel ingot, drawing out the steel ingot for one time after upsetting, and then returning to a furnace for homogenizing to obtain a first-upset and first-drawn blank; after the blank is taken out of the furnace, upsetting the blank again until the height of the first upsetting first-drawing blank is 1/3-1/2, upsetting the blank, drawing the blank again, returning the blank to the furnace and homogenizing to obtain a second upsetting second-drawing blank; after discharging, upsetting for the third time, upsetting to 1/3-1/2 of the height of the two-upsetting two-drawing blank, drawing out for the third time after upsetting, and then returning to the furnace for homogenizing;
and step S3, performing spheroidizing annealing treatment on the billet to obtain an annealed billet.
Specifically, step S3 includes: placing the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800-850 ℃ (such as 800 ℃) at 8-12 ℃/min (such as 10 ℃/min), then preserving heat for 20-40min (such as 30min), then heating to 860-880 ℃ (such as 860 ℃) at 8-12 ℃/min (such as 10 ℃/min), preserving heat for 80-100min (such as 90 min); cooling to 730-750 deg.C (such as 750 deg.C) at 2-4 deg.C/min (such as 3 deg.C/min), maintaining for 80-100min (such as 90min), cooling to 550-600 deg.C at 25-30 deg.C/h, and air cooling to room temperature.
In step 3, the temperature is gradually raised to 860 ℃ in stages, and the austenite phase with a proper size is obtained through the stage heat preservation, so that the ingot is cracked when the temperature raising rate is too high, the structure is coarse when the temperature raising rate is too low, the structure is coarse when the heating temperature is too high, the austenite structure cannot be obtained when the heating temperature is too low, the structure is coarse when the heat preservation time is too long, and the structure is not sufficiently homogenized when the heat preservation time is too short.
The spheroidizing annealing is performed for the purpose of obtaining a spherical or granular carbide structure, refining grains, reducing hardness, improving machinability, and preparing a structure for subsequent quenching, and the stainless steel material after spheroidizing annealing has a granular pearlite structure.
And step S4, quenching and tempering the annealed steel billet to obtain the final steel billet.
The specific quenching and tempering treatment is oil quenching and secondary tempering, and the step S4 includes: putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800-810 ℃ (such as 800 ℃) at 8-12 ℃/min (such as 10 ℃/min), then preserving heat for 20-40min (such as 30min), then heating to 1030-1130 ℃ at 8-12 ℃/min (such as 10 ℃/min), preserving heat for 20-40min (such as 30min), and finally performing oil quenching to room temperature; after aging for 1-2h at room temperature, tempering.
Specifically, the tempering comprises: reheating to 250-450 ℃, preserving heat for 2h, and then air-cooling to room temperature; then heating to 250-450 ℃, preserving heat for 2h, and then cooling to room temperature again.
The purpose of the oil quenching and the secondary tempering heat treatment is to obtain tempered martensite and retained austenite. The heat treatment process of the invention ensures that the average grain size of the tempered martensite is 28-32 mu m (30 mu m) and is about 1/2 of the grain size of the existing 40Cr13 stainless steel, thereby improving various mechanical properties of the stainless steel material, specifically the tensile strength is 1745-1825MPa (such as 1780MPa), the yield strength is 1370-1463MPa (such as 1415MPa), the elongation is 8.5-9.3% (such as 9.1%), and the impact work is 25-33J/cm2(30.3J/cm2) For example, the hardness is 50-52HRC (such as 51.7HRC), and compared with the existing 40Cr13 stainless steel, the tensile strength is improved by 27.7% -33.5% (such as 30%), the elongation is improved by 0.89-1.07 times (such as 1 time), and the hardness is improved by 15% -19.5% (such as 18%).
Or the specific quenching and tempering treatment is isothermal quenching and tempering, and the step 4 comprises the following steps: and (3) putting the annealed steel billet obtained in the step (3) into a heat treatment furnace, heating to 800-810 ℃ (such as 800 ℃) at 8-12 ℃/min (such as 10 ℃/min), preserving heat for 20-40min (such as 30min), then heating to 1030-1130 ℃ at 8-12 ℃/min (such as 10 ℃/min), preserving heat for 20-40min (such as 30min), then quickly putting into a salt bath furnace with the temperature of T1, continuously preserving heat for T2 time in the salt bath furnace, finally taking out, air cooling to room temperature, and tempering.
Specifically, T1 is 180-280 ℃, T2 is 60-300min, and tempering comprises the following steps: reheating to 250-450 ℃, preserving heat for 2h, and then air cooling to room temperature.
It should be noted that the purpose of the austempering and tempering treatment is to obtain a bainite structure, after the austempering and tempering treatment, the structure of the stainless steel material is a carbide-free bainite structure, the average grain size is 26-30 μm (such as 28 μm), the mechanical properties of the stainless steel cutting material are further improved, and the specific tensile strength is 1819-1867MPa (such as 1840MPa), the yield strength is 1480-1563MPa (such as 1531.8MPa), the elongation is 10-12% (such as 11.1%), and the impact work is 36-41J/cm2(e.g., 38.7J/cm)2) The hardness is 52.2-54HRC (such as 53.4HRC), and compared with the existing 40Cr13 stainless steel, the tensile strength is improved by 33.1-36.6 percent (such as 34 percent), the elongation is improved by about 1.22-1.67 times (such as 1.5 times), and the hardness is improved by 20-24 percent (such as 22 percent).
Example 1
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, loading scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1550 ℃, casting when the temperature is reduced to 1420 ℃, obtaining cast ingots with the diameter phi of 70mm, and carrying out air cooling.
Step S2, heating the cast ingot to 1150 ℃, preserving heat for 2 hours, homogenizing, forging, wherein the initial forging temperature is 1050 ℃, the final forging temperature is 850 ℃, three piers and three pulls are adopted in the forging process, a steel billet with the diameter phi of 45mm is obtained after forging, and the steel billet is air-cooled to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 550 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1030 ℃ at a speed of 10 ℃/min, preserving heat for 30min, and finally performing oil quenching to room temperature; after aging for 2h at room temperature, reheating to 250 ℃, preserving heat for 2h, and then air-cooling to room temperature; heating to 250 deg.C, keeping the temperature for 2h, and air cooling to room temperature. The mechanical properties and the microstructure of the high-silicon stainless steel material containing vanadium and titanium are shown in Table 2, the metallographic structure diagram is shown in figure 1, the scanning structure diagram is shown in figure 2, and the grain size microscopic image is shown in figure 14.
Example 2
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, charging scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1600 ℃, casting when the temperature is reduced to 1440 ℃, obtaining cast ingots with the diameter phi of 80mm, and carrying out air cooling.
Step S2, heating the cast ingot to 1180 ℃, preserving heat for 1.5 hours, homogenizing, forging, wherein the initial forging temperature is 1060 ℃, the final forging temperature is 870 ℃, three-pier three-drawing is adopted in the forging process, a billet with the diameter phi of 47mm is obtained after forging, and air cooling is carried out to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 570 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1050 ℃ at a speed of 10 ℃/min, preserving heat for 30min, and finally oil quenching to room temperature; after aging at room temperature for 1.5h, reheating to 350 ℃, preserving heat for 2h, and then air cooling to room temperature; heating to 350 deg.C, keeping the temperature for 2h, and air cooling to room temperature. The mechanical properties and the microstructure of the high-silicon stainless steel material containing vanadium and titanium are shown in Table 2, a metallographic structure diagram is shown in figure 3, and a scanning structure diagram is shown in figure 4.
Example 3
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, charging scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1620 ℃, casting when the temperature is reduced to 1450 ℃, obtaining cast ingots with the diameter of phi 90mm, and carrying out air cooling.
Step S2, heating the cast ingot to 1150 ℃, preserving heat for 1h, homogenizing, forging, wherein the initial forging temperature is 1080 ℃, the final forging temperature is 900 ℃, three piers and three pulls are adopted in the forging process, a steel billet with the diameter phi of 50mm is obtained after forging, and the steel billet is air-cooled to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 600 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1100 ℃ at a speed of 10 ℃/min, preserving heat for 30min, and finally oil quenching to room temperature; after aging at room temperature for 1h, reheating to 450 ℃, preserving heat for 2h, and then air-cooling to room temperature; heating to 450 ℃, preserving heat for 2 hours, and then cooling in air to room temperature again to obtain the product. The mechanical properties and the microstructure of the high-silicon vanadium-titanium-containing stainless steel knife-shear material are shown in a table 2, a metallographic structure diagram is shown in a figure 5, and a scanning structure diagram is shown in a figure 6.
Example 4
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, loading scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1550 ℃, casting when the temperature is reduced to 1420 ℃, obtaining cast ingots with the diameter phi of 70mm, and carrying out air cooling.
Step S2, heating the cast ingots to 1150 ℃, preserving heat for 2 hours, homogenizing, forging, wherein the initial forging temperature is 1050 ℃, the final forging temperature is 850 ℃, three-pier three-drawing is adopted in the forging process, a steel billet with the diameter phi of 45mm is obtained after forging, and air cooling is carried out to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 550 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
And S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1030 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then quickly putting into a 180 ℃ salt bath furnace, continuing preserving heat for 60min in the salt bath furnace, finally taking out, air-cooling to room temperature, reheating to 250 ℃, preserving heat for 2h, and then air-cooling to room temperature. The mechanical properties and the microstructure of the high-silicon stainless steel material containing vanadium and titanium are shown in Table 2, the metallographic structure diagram is shown in FIG. 7, the scanning structure diagram is shown in FIG. 8, and the grain size microscopic image is shown in FIG. 15.
Example 5
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, charging scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1600 ℃, casting when the temperature is reduced to 1440 ℃, obtaining cast ingots with the diameter phi of 80mm, and carrying out air cooling.
Step S2, heating the cast ingot to 1180 ℃, preserving heat for 1.5 hours, homogenizing, forging, wherein the initial forging temperature is 1060 ℃, the final forging temperature is 870 ℃, three-pier three-drawing is adopted in the forging process, a billet with the diameter phi of 47mm is obtained after forging, and air cooling is carried out to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 570 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
And S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1050 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then quickly putting into a 220 ℃ salt bath furnace, continuing preserving heat for 180min in the salt bath furnace, finally taking out and air-cooling to room temperature, reheating to 350 ℃, preserving heat for 2h, and then air-cooling to room temperature. The mechanical properties and the microstructure of the high-silicon stainless steel material containing vanadium and titanium are shown in Table 2, a metallographic structure diagram is shown in figure 9, and a scanning structure diagram is shown in figure 10.
Example 6
The chemical composition of the steel of this example is shown in table 1, and the preparation method comprises the following steps:
and step S1, charging scrap steel, pig iron, ferrochromium and nickel blocks into an induction smelting furnace according to the alloy component ratio, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device to carry out vacuum smelting when molten steel is dissolved clearly, raising the highest temperature of the molten steel to 1620 ℃, casting when the temperature is reduced to 1450 ℃, obtaining cast ingots with the diameter of phi 90mm, and carrying out air cooling.
Step S2, heating the cast ingot to 1150 ℃, preserving heat for 1h, homogenizing, forging, wherein the initial forging temperature is 1080 ℃, the final forging temperature is 900 ℃, three piers and three pulls are adopted in the forging process, a steel billet with the diameter phi of 50mm is obtained after forging, and the steel billet is air-cooled to the room temperature;
s3, putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 860 ℃ at a speed of 10 ℃/min, and preserving heat for 90 min; then cooling to 750 ℃ at the speed of 3 ℃/min, preserving heat for 90min, cooling to 600 ℃ at the speed of 25-30 ℃/h, and finally taking out and air-cooling to room temperature.
And S4, putting the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then heating to 1100 ℃ at a speed of 10 ℃/min, preserving heat for 30min, then quickly putting into a 280 ℃ salt bath furnace, continuing preserving heat for 300min in the salt bath furnace, finally taking out and air-cooling to room temperature, reheating to 450 ℃, preserving heat for 2h, and then air-cooling to room temperature. The mechanical properties and the microstructure of the high-silicon stainless steel material containing vanadium and titanium are shown in Table 2, a metallographic structure diagram is shown in figure 11, and a scanning structure diagram is shown in figure 12.
Table 1 chemical composition Wt.% of examples 1-6 steels and comparative example 40Cr 13%
Steel grade C Si Mn Cr Ni V Ti S P
Example 1 0.40 1.48 0.79 10.57 0.23 - 0.06 0.02 0.03
Example 2 0.37 1.05 0.93 13.01 0.45 0.15 - 0.03 0.01
Example 3 0.38 1.83 0.62 11.88 0.59 0.10 0.20 0.01 0.02
Example 4 0.40 1.58 0.75 10.67 0.22 - 0.17 0.02 0.03
Example 5 0.36 1.01 0.90 13.00 0.47 0.05 - 0.03 0.01
Example 6 0.35 1.63 0.66 12.97 0.55 0.20 0.10 0.01 0.02
Comparative example 1 0.36 0.45 0.18 12.52 0.51 - - 0.02 0.03
Comparative example 2 0.40 0.52 0.32 13.57 0.29 - - 0.02 0.02
TABLE 2 mechanical properties and microstructures of the steels of examples 1-6 and comparative example 40Cr13
Figure BDA0003260173040000161
Figure BDA0003260173040000171
In addition, the comparison of the grain sizes of fig. 13, 14 and 15 shows that the grain sizes of 1/2 of 40Cr13 are 30 μm and 28 μm respectively, which is also the important reason for the improvement of the mechanical properties.

Claims (10)

1. The high-silicon stainless steel material containing vanadium and titanium is characterized by comprising the following components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0-0.20%, V: 0-0.20 percent of Ti and V, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities, wherein at least one of Ti and V is added in the required content range.
2. The high-silicon vanadium-titanium-containing stainless steel material as claimed in claim 1, wherein the stainless steel material comprises the following components in percentage by mass: c: 0.35% -0.40%, Si: 1.00% -2.00%, Mn: 0.60% -1.00%, Cr: 10.00% -13.00%, Ni: 0.20% -0.60%, Ti: 0.10% -0.20%, V: 0.10 to 0.20 percent of the total weight of the alloy, less than or equal to 0.03 percent of S, less than or equal to 0.03 percent of P, and the balance of Fe and inevitable trace impurities.
3. A method for preparing a high-silicon vanadium-titanium-containing stainless steel material, which is used for preparing the stainless steel material of claims 1 and 2, and comprises the following steps:
step S1, smelting molten steel, and then casting to obtain a cast ingot;
step S2, forging the cast ingot to obtain a steel billet;
step S3, carrying out spheroidizing annealing treatment on the steel billet to obtain an annealed steel billet;
and step S4, quenching and tempering the annealed steel billet to obtain a final steel billet, wherein the quenching and tempering are oil quenching and secondary tempering or isothermal quenching and tempering.
4. The method for preparing high-silicon stainless steel material containing vanadium and titanium according to claim 3, wherein the step S1 comprises: and (2) putting the scrap steel, pig iron, ferrochrome and nickel blocks into an induction smelting furnace, after molten steel is dissolved, sequentially adding ferrosilicon, ferromanganese, titanium wires and ferrovanadium through a secondary feeding device for vacuum smelting, raising the highest temperature of the molten steel to 1550-.
5. The method for preparing high-silicon stainless steel material containing vanadium and titanium according to claim 3, wherein the step S2 comprises: heating the ingot obtained in the step S1 to 1150-1180 ℃, preserving heat for 1-2h for homogenization, then forging, wherein the initial forging temperature is 1050-1100 ℃, the final forging temperature is 850-900 ℃, three-dun three-drawing is adopted in the forging process, and the billet obtained after forging is air-cooled to room temperature.
6. The method for preparing high-silicon stainless steel material containing vanadium and titanium according to claim 3, wherein the step S3 comprises: putting the steel billet obtained in the step S2 into a heat treatment furnace, heating to 800-850 ℃, preserving heat, and then heating to 860-880 ℃ for heat preservation; then cooling to 730-750 deg.C, heat-insulating, cooling to 550-600 deg.C, finally taking out and air-cooling to room temperature.
7. The method for preparing a high-silicon stainless steel material containing vanadium and titanium according to claim 3, wherein in step S4, the quenching and tempering treatment is oil quenching and secondary tempering;
the quenching comprises the following steps: placing the annealed steel billet obtained in the step S3 into a heat treatment furnace, heating to 800-; aging at room temperature for 1-2h, and then carrying out secondary tempering;
the secondary tempering comprises: reheating to 250-450 ℃, preserving heat for 1.8-2.2h, and then air-cooling to room temperature; then heating to 250-450 deg.C, heat-insulating for 1.8-2.2h, then air-cooling again to room temperature.
8. The method for preparing the high-silicon stainless steel material containing vanadium and titanium according to claim 7, wherein after oil quenching and secondary tempering treatment, the microstructure is tempered martensite and retained austenite.
9. The method for preparing a high-silicon stainless steel material containing vanadium and titanium according to claim 3, wherein in step S4, the quenching and tempering treatment is isothermal quenching and tempering;
the quenching comprises the following steps: placing the steel billet obtained in the step S3 into a heat treatment furnace, heating to 800-;
the tempering comprises: reheating to 250-450 ℃, preserving heat for 2h, and then air cooling to room temperature.
10. The method for preparing a high-silicon stainless steel material containing vanadium and titanium according to claim 9, wherein the microstructure is bainite after the austempering plus tempering treatment.
CN202111070811.5A 2021-09-13 2021-09-13 High-silicon stainless steel material containing vanadium and titanium and preparation method thereof Active CN114457284B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202111070811.5A CN114457284B (en) 2021-09-13 2021-09-13 High-silicon stainless steel material containing vanadium and titanium and preparation method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202111070811.5A CN114457284B (en) 2021-09-13 2021-09-13 High-silicon stainless steel material containing vanadium and titanium and preparation method thereof

Publications (2)

Publication Number Publication Date
CN114457284A true CN114457284A (en) 2022-05-10
CN114457284B CN114457284B (en) 2022-07-19

Family

ID=81405423

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202111070811.5A Active CN114457284B (en) 2021-09-13 2021-09-13 High-silicon stainless steel material containing vanadium and titanium and preparation method thereof

Country Status (1)

Country Link
CN (1) CN114457284B (en)

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103614649A (en) * 2013-12-06 2014-03-05 东北大学 High-strength, high-toughness and high-plasticity martensitic stainless steel and preparation method thereof
CN106906429A (en) * 2017-03-01 2017-06-30 西安交通大学 A kind of superhigh intensity martensitic stain less steel and preparation method thereof
CN109594022A (en) * 2018-11-14 2019-04-09 育材堂（苏州）材料科技有限公司 High-strength stainless steel, heat treatment process and formed parts
US20200063247A1 (en) * 2012-10-24 2020-02-27 Crs Holdings, Inc. Quench and Temper Corrosion Resistant Steel Alloy and Method for Producing the Alloy
CN112593157A (en) * 2020-12-09 2021-04-02 暨南大学 High-toughness bainite wear-resistant cast steel and preparation method and application thereof

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20200063247A1 (en) * 2012-10-24 2020-02-27 Crs Holdings, Inc. Quench and Temper Corrosion Resistant Steel Alloy and Method for Producing the Alloy
CN103614649A (en) * 2013-12-06 2014-03-05 东北大学 High-strength, high-toughness and high-plasticity martensitic stainless steel and preparation method thereof
CN106906429A (en) * 2017-03-01 2017-06-30 西安交通大学 A kind of superhigh intensity martensitic stain less steel and preparation method thereof
CN109594022A (en) * 2018-11-14 2019-04-09 育材堂（苏州）材料科技有限公司 High-strength stainless steel, heat treatment process and formed parts
CN112593157A (en) * 2020-12-09 2021-04-02 暨南大学 High-toughness bainite wear-resistant cast steel and preparation method and application thereof

Also Published As

Publication number Publication date
CN114457284B (en) 2022-07-19

Similar Documents

Publication Publication Date Title
EP2562283B1 (en) Steel part having excellent in temper softening resistance
CN109023119A (en) A kind of abrasion-resistant stee and its manufacturing method with excellent plasticity and toughness
CN111748739B (en) Heat-resistant spring steel with tensile strength of more than 2100MPa and production method thereof
CN109763078B (en) Heat-resistant alloy carburizing steel and preparation method thereof
CN113249645B (en) High-ductility and ultrahigh-strength ductile steel and preparation method thereof
CN114717488A (en) 1800MPa grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
WO2022228216A1 (en) Steel for high-temperature carburized gear shaft and manufacturing method for steel
AU2022392619A1 (en) High-strength steel with good weather resistance and manufacturing method therefor
CN113774281A (en) 2000 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
CN113774280A (en) 2400 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
WO2021208181A1 (en) Low-temperature, high-toughness, high-temperature, high-intensity and high-hardenability hot mold steel and preparation method therefor
CN111850399A (en) Corrosion-resistant plastic die steel with good wear resistance and preparation method thereof
CN113061815B (en) 800 MPa-grade quenched and tempered high-strength steel with stable full-section impact performance and production method thereof
CN113667905A (en) Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof
CN114457283B (en) High-silicon vanadium-titanium-containing stainless steel knife and shear material and preparation method thereof
CN117210771B (en) Thick high-performance nitrogen-containing austenitic stainless steel for nuclear power and manufacturing method thereof
CN113774291A (en) Ultra-low carbon high-performance maraging stainless steel and preparation method thereof
CN113699464A (en) Ultra-high-strength high-performance sheet maraging stainless steel and preparation method thereof
CN111996462A (en) Longitudinal variable-thickness ultrahigh-strength ship board and production method thereof
CN114058960B (en) High-strength high-toughness easy-welding nano steel with thickness of 25-60 mm and thickness of 1000MPa and preparation method thereof
CN115261734A (en) High-homogeneity non-quenched and tempered steel for engineering machinery and production method
CN114457284B (en) High-silicon stainless steel material containing vanadium and titanium and preparation method thereof
CN115558863A (en) Marine steel with yield strength of more than or equal to 750MPa and low yield ratio and production process thereof
CN114703431A (en) Heat treatment process for homogenizing hot-work die steel and annealing structure
CN111850413B (en) Preparation method of easily-welded fatigue-resistant high-strength and high-toughness alloy steel

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant