CN113930672A - Corrosion-resistant high-strength stainless steel and manufacturing method thereof - Google Patents

Corrosion-resistant high-strength stainless steel and manufacturing method thereof Download PDF

Info

Publication number
CN113930672A
CN113930672A CN202111059425.6A CN202111059425A CN113930672A CN 113930672 A CN113930672 A CN 113930672A CN 202111059425 A CN202111059425 A CN 202111059425A CN 113930672 A CN113930672 A CN 113930672A
Authority
CN
China
Prior art keywords
temperature
equal
less
percent
stainless steel
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.)
Withdrawn
Application number
CN202111059425.6A
Other languages
Chinese (zh)
Inventor
张景海
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.)
Individual
Original Assignee
Individual
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 Individual filed Critical Individual
Priority to CN202111059425.6A priority Critical patent/CN113930672A/en
Publication of CN113930672A publication Critical patent/CN113930672A/en
Withdrawn legal-status Critical Current

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • 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
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • C22B9/04—Refining by applying a vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • C22B9/16—Remelting metals
    • C22B9/20—Arc remelting
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Abstract

The invention discloses corrosion-resistant high-strength stainless steel and a manufacturing method thereof, which relate to the technical field of engineering materials and comprise the following chemical components in percentage by weight: c: 0.03 to 0.20%, Ni: 2.50-13.00%, Cr: 11.50-13.50%, Mo: 4.00-6.00%, W: 0.50-1.50%, Co: 11.00-13.50%, Al: less than or equal to 2.00 percent, Nb: less than or equal to 0.10 percent, V: less than or equal to 0.25 percent, Ti: less than or equal to 0.005 percent, N: less than or equal to 0.0020 percent, O: less than or equal to 0.0015 percent, Mn: 0.10%, Si: less than or equal to 0.10 percent, S: less than or equal to 0.002%, P: less than or equal to 0.006 percent, and the balance of Fe and other inevitable impurity elements; according to the chemical composition proportion of stainless steel, vacuum induction smelting is adopted, electrodes are cast, a vacuum consumable remelting steel ingot is subjected to vacuum consumable remelting, steel ingot diffusion annealing, forging, fast forging, cogging, forming and annealing. The stainless steel has the advantages of improving the strength of the steel without reducing the ductility and toughness, improving the corrosion resistance and prolonging the service life, and the strength grade is 1900-2400 Mpa.

Description

Corrosion-resistant high-strength stainless steel and manufacturing method thereof
Technical Field
The invention relates to the technical field of engineering materials, in particular to corrosion-resistant high-strength stainless steel and a manufacturing method thereof.
Background
The demand of the ultra-high strength stainless steel resistant to the marine climate in the ocean engineering is more and more urgent, and particularly, the stress corrosion resistance of the important stressed structural member of the machine serving in the ocean environment is more and more emphasized, for example, the A-100(23Co13Ni11Cr3Mo) steel for a certain part generates pitting corrosion on the exposed surface in the ocean environment for two days, and the pitting corrosion part is easy to generate hydrogen embrittlement under the action of stress to cause the part to lose efficacy, so that the research and development of novel ultra-high strength stainless steel is very urgent.
The Zhao Zhen of Beijing Hooker in the nineties invents stainless steel of 0.07-0.1C, 12-14Cr, 2-6Co, 3.5-5.5Mo, 0.80-1.2W, 0.05-0.25V and 0.05-0.15 Nb; the strength of the steel reaches above 1900 MPA;
s53(20Cr10Co14Ni5Mo2WV) is steel for the landing gear of the shipboard aircraft of the United states invention, but the corrosion resistance of the material is not very good due to low chromium and slightly high carbon;
the Schlenk et al found that S280(0.1C, 2.5Ni, 12.5Cr, 12Co, 4.5Mo, 1W, 0.25V) steel has better mechanical property and corrosion resistance than S53 steel, but the steel has the defects of low yield strength and yield ratio of only 0.8;
liu Zhenbao etc. invented the marine environment corrosion resistant high strength stainless steel (0.03C, Cr12.5, Ni4.5, Mo5, Co14.5, 0.4Ti, strength is greater than 1900MPA grade super strength stainless steel), adopt quenching to obtain martensite matrix and age-hardening to improve the performance of the steel, but the material contains titanium, the aging process forms Ni3Ti to improve the strength, but Ti makes the ductility and toughness of the steel reduced.
Based on the above problems, we have devised a corrosion-resistant high-strength stainless steel and a method for manufacturing the same to solve the above problems.
Disclosure of Invention
The invention aims to solve the defects in the prior art, and provides corrosion-resistant high-strength stainless steel and a manufacturing method thereof, which are used for manufacturing important stressed structural components serving in a marine environment, meet the increasing requirements of marine engineering, improve the corrosion resistance of parts and prolong the service life of the parts.
The first purpose is to provide a corrosion-resistant high-strength stainless steel, which adopts the following technical scheme:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.03 to 0.20%, Ni: 2.50-13.00%, Cr: 11.50-13.50%, Mo: 4.00-6.00%, W: 0.50-1.50%, Co: 11.00-13.50%, Al: less than or equal to 2.00 percent, Nb: less than or equal to 0.10 percent, V: less than or equal to 0.25 percent, Ti: less than or equal to 0.005 percent, N: less than or equal to 0.0020 percent, O: less than or equal to 0.0015 percent, Mn: 0.10%, Si: less than or equal to 0.10 percent, S: less than or equal to 0.002%, P: less than or equal to 0.006 percent, and the balance of Fe and other inevitable impurity elements.
C is subjected to solid solution strengthening and forms carbide strengthening during tempering, C mainly improves the strength, a certain amount of carbon forms VC and NbC refined grains, a certain amount of carbon reacts with carbon and oxygen during vacuum smelting to generate CO, the CO gas floats upwards to drive nitrogen to be removed, the carbon plays a role in degassing, but the high carbon can reduce the corrosion resistance and the plastic toughness of the steel.
Cr reduces the critical cooling speed, improves the hardenability, enables the material to obtain a martensite structure at room temperature, obviously improves the oxidation resistance of the steel, and plays a decisive role in the corrosion resistance of the steel, but Cr is a ferrite forming element, and the strength of the steel can be influenced by the over-high content of Cr.
Mo increases the secondary hardening effect, improves the strength without reducing the toughness, improves the passivation effect of Cr, inhibits the pitting tendency of chloride ions, improves the intergranular corrosion resistance, particularly improves the pitting resistance, and is a ferrite forming element. In martensitic stainless steel, Mo can increase the tempering stability and the secondary hardening effect while increasing the strength of the steel without decreasing the toughness.
W is a ferrite-forming element and a strong carbide-forming element, and improves the strength, particularly the yield strength of the steel, without reducing the ductility and toughness. W in martensitic stainless steel can increase the tempering stability and improve the high-temperature resistance of the steel, and has the capability of improving the pitting corrosion resistance like Mo.
Ni expands a gamma phase region, and guarantees that martensite structures can be obtained at any cooling speed after solid solution and austenitization; the toughness is improved, Ni3Al and Ni3Mo strengthening phases are obtained after aging treatment, the Ni solid solution strengthening and aging strengthening effects are obvious, and the strength of the steel is improved.
Co solid solution strengthening promotes the precipitation of Mo metal type compounds (Ni3Mo) and inhibits the austenite recovery in the aging process, and the joint action of CoMo strengthens the matrix and can improve the ductility and toughness; the strength of Co increases by 5.95MPA for every 1% increase when Co is greater than 6%.
Ni3Al strengthening phase is precipitated during Al aging, the strengthening phase only improves the strength but does not reduce the ductility and toughness,
v, Nb form carbide element strongly, and refined grains are added properly. The carbide is difficult to dissolve, the quenching temperature is increased to coarsen the crystal grains, and V, Nb cannot be too high.
Ti is easy to form Ti (CN) to reduce the ductility and toughness, Ni3Ti needle-shaped precipitation boundary formed by aging improves the strength but reduces the ductility and toughness, and the sulfur nitrogen oxide phosphorus reduces the ductility and toughness of the steel and is strictly controlled.
By adopting the technical scheme: the invention contains Ni, Co, Ni, Co and matrix solid solution to form solid solution strengthening, a highly distorted martensite matrix is obtained by quenching, the martensite matrix precipitates carbides (M2C) after tempering containing strong carbide forming elements W, Mo, Nb, V and Cr, Ni3Al strengthening phase is obtained after tempering containing Al, meanwhile, the ductility and toughness are not reduced, the strength is greatly improved, meanwhile, the invention contains 12-14% of chromium with corrosion resistance, oxygen and nitrogen elements are strictly controlled in the smelting process to avoid forming a plurality of oxides and nitrides, and meanwhile, the nitrogen and oxygen content is controlled to have high corrosion resistance; the invention has another characteristic of high pitting corrosion resistance, which is originated from the chemical composition and the structural uniformity of the material in the metallurgical material, and the addition of W, Mo improves the pitting corrosion resistance of the steel.
The second purpose is to provide a manufacturing method of the corrosion-resistant high-strength stainless steel, which adopts the following technical scheme:
the method for manufacturing the corrosion-resistant high-strength stainless steel comprises the following steps:
according to the chemical composition proportion of stainless steel, vacuum induction smelting is adopted, electrodes are cast, a vacuum consumable remelting steel ingot is subjected to vacuum consumable remelting, steel ingot diffusion annealing, forging, fast forging, cogging, forming and annealing.
Furthermore, a vacuum induction furnace is used in vacuum induction smelting, and furnace charges of the vacuum induction furnace are selected from high-purity low-sulfur-phosphorus aluminum-titanium metal chromium, nickel, cobalt, molybdenum, tungsten, vanadium, niobium and aluminum and low-sulfur, phosphorus, silicon, manganese, aluminum and titanium pure iron/refined steel furnace charges.
Furthermore, a pure iron is needed to wash the vacuum induction furnace before the formal smelting, and the electric melting is started in the vacuum induction furnace under the vacuum degree of less than or equal to 2.7 Pa.
Further, the vacuum induction melting process parameters are as follows:
and (3) charging sequence: charging a small amount of pure iron-Ni and Co plates-pure iron-metal Mo, W, V and C, feeding power after the Ni and Co plates are charged, charging the rest materials after the Ni and Co plates are slightly red, reserving all Cr and Al during charging, adding fine adjustment components of Cr and Nb after full melting, refining after the Cr and Nb are fully melted, wherein the refining time is more than or equal to 45 minutes, the temperature is controlled to 1570 and 1590 ℃ in the refining period, sampling and analyzing chemical components after refining is finished, adding carbon and aluminum and the like, fully stirring after the carbon and aluminum are fully melted, measuring the temperature, tapping, and controlling the pouring temperature: liquidus +20-70 deg.C;
further, the technological parameters of the cast electrode are as follows:
casting phi 440 and phi 580 electrodes;
after the electrode is poured, the vacuum is kept for 40 minutes, then the electrode is broken, and the mold is cooled for 5 hours, demolded and annealed in a red sending way;
and (3) annealing process of the electrode: the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at the speed of less than or equal to 80 ℃/h, the temperature is kept for 20h, the temperature is gradually decreased to 500 ℃, and the mixture is taken out of the furnace for air cooling.
Further, the consumable remelting ingot process comprises the following steps:
polishing the surface of the electrode, and cleaning;
phi 508mm and phi 660mm of the consumable crystallizer;
the filling process comprises the following steps: the capping weight is 250-350kg, and the capping time is 60-90 minutes;
and (3) a cooling process: cooling under vacuum for 40min, breaking vacuum, cooling under non-vacuum for 40min, and demolding;
further, the steel ingot diffusion annealing process parameters are as follows:
the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at the speed of less than or equal to 80 ℃/h, the temperature is maintained at the temperature for more than or equal to 25h, the temperature is gradually decreased to 500 ℃, and the mixture is discharged from the furnace and cooled;
and (4) polishing or polishing the surface of the self-consumption ingot after annealing.
Further, the technological parameters of forging, rapid forging, cogging and forming are as follows:
the heating curve of the steel ingot is as follows: keeping the steel ingot at the temperature of less than or equal to 600 ℃ for 1h, gradually increasing the temperature to 900 +/-10 ℃ within 3h or more, maintaining the temperature for 2h, gradually increasing the temperature to 1250 +/-20 ℃ within 4h or more, maintaining the temperature for 35h or more, gradually decreasing the temperature to 1200 +/-10 ℃ within 2 h;
first upsetting and drawing out: tapping the steel ingot, upsetting, drawing down to an intermediate size (the height-diameter ratio is 2.5-2.8) with the reduction of 40-60%; returning to 1180 +/-10 ℃ and preserving heat for 90-120 minutes;
and (3) upsetting and drawing for the second time: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn to be of an intermediate size (the height-diameter ratio is 2.5-2.8); returning to 1180 +/-10 ℃ and preserving heat for 90-120 minutes;
third upsetting and drawing out: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn out to be octagonal with the thickness of 450-490; the furnace is returned to 1050 +/-50 ℃ and the temperature is preserved for 120-150 minutes;
drawing to phi 300, and the final forging temperature is more than or equal to 750 ℃;
after forging, air cooling is carried out until the temperature is less than or equal to 200 ℃, and annealing is carried out in a furnace.
Further, the annealing process parameters are as follows:
when the materials are to be charged, the temperature is between 300 ℃ and 500 ℃, the temperature is increased to 950 +/-10 ℃ within more than or equal to 6 hours at the temperature increasing speed of less than or equal to 100 ℃/h, the temperature is maintained at the temperature for more than or equal to 3 hours, the temperature is cooled to less than or equal to 200 ℃ for remelting, the temperature is gradually increased to 630 ℃ and 680 ℃, the temperature is maintained at the temperature for more than or equal to 15 hours, and then the materials are discharged from the furnace for air cooling.
By adopting the technical scheme: the strength of the steel is improved by combining martensite solid solution strengthening, secondary hardening and aging strengthening; w, Al elements are added to improve the yield strength; w, Mo elements are added to improve the pitting corrosion resistance and the high temperature resistance; in order to improve the corrosion resistance, the oxygen and nitrogen content is strictly controlled to improve the purity, and the high purity obviously improves the ductility and toughness of the steel. The invention adopts the vacuum induction furnace and the vacuum consumable electrode furnace for smelting, the component control accuracy is high, the gas content of the steel is effectively reduced by high vacuum degree, and the uniformity of the components of the structure is improved by high cooling speed.
Compared with the prior art, the invention has the beneficial effects that:
the stainless steel improves the strength of the steel, does not reduce the plasticity and toughness, has the strength level of 1900-2400MPa, improves the corrosion resistance, and further prolongs the service life.
Drawings
FIG. 1 is a graph of electrode annealing temperature for a cast electrode process parameter of the present invention;
FIG. 2 is a temperature profile of a steel ingot diffusion annealing process according to the present invention;
FIG. 3 is a steel ingot heating curve of the forging, rapid forging, cogging and rolling process of the present invention;
fig. 4 is a temperature profile of an annealing process in the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments.
The invention discloses corrosion-resistant high-strength stainless steel.
The corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.03 to 0.20%, Ni: 2.50-13.00%, Cr: 11.50-13.50%, Mo: 4.00-6.00%, W: 0.50-1.50%, Co: 11.00-13.50%, Al: less than or equal to 2.00 percent, Nb: less than or equal to 0.10 percent, V: less than or equal to 0.25 percent, Ti: less than or equal to 0.005 percent, N: less than or equal to 0.0020 percent, O: less than or equal to 0.0015 percent, Mn: 0.10%, Si: less than or equal to 0.10 percent, S: less than or equal to 0.002%, P: less than or equal to 0.006 percent, and the balance of Fe and other inevitable impurity elements.
Wherein, C: 0.03-0.20 wt%, solid solution strengthening and carbide strengthening formed during tempering, wherein C mainly improves the strength, a certain carbon content forms VC and NbC refined grains, a certain amount of carbon reacts with carbon and oxygen to generate CO during vacuum smelting, the CO gas floats upwards to drive the removal of nitrogen, the carbon plays a role in degassing, but the high carbon content can reduce the corrosion resistance and the plastic toughness of the steel.
Cr: 12.00-14.00 wt%, Cr reduces critical cooling speed, improves hardenability, enables the material to obtain martensite structure at room temperature, obviously improves the oxidation resistance of steel, and plays a decisive role in the corrosion resistance of steel, but Cr is a ferrite forming element, and the strength of steel can be influenced by overhigh Cr content.
Mo: 4-6 wt%, Mo increases the secondary hardening effect, improves the strength without reducing the toughness, improves the passivation effect of Cr, inhibits the pitting tendency of chloride ions, improves the intergranular corrosion resistance, particularly improves the pitting corrosion resistance, and is a ferrite forming element. In martensitic stainless steel, Mo can increase the tempering stability and the secondary hardening effect while increasing the strength of the steel without decreasing the toughness.
W: 0.5-1.5 wt%, W is ferrite forming element, strong carbide forming element, and can raise strength, specially raise yield strength of steel, and at the same time does not reduce plasticity and toughness. W in martensitic stainless steel can increase the tempering stability and improve the high-temperature resistance of the steel, and has the capability of improving the pitting corrosion resistance like Mo.
Ni: 2.50-13 wt%, Ni expands gamma phase region to ensure that martensite structure can be obtained at any cooling speed after solid solution and austenitization; the toughness is improved, Ni3Al and Ni3Mo strengthening phases are obtained after aging treatment, the Ni solid solution strengthening and aging strengthening effects are obvious, and the strength of the steel is improved.
Co: 10.00-14.00 wt%, solid solution strengthening, Mo metal type compound (Ni3Mo) precipitation is promoted, austenite recovery in the aging process is inhibited, and the Co-action of CoMo strengthens the matrix and can improve the plastic toughness and the plastic toughness; the strength of Co increases by 5.95MPA for every 1% increase when Co is greater than 6%.
Al: less than or equal to 2.00wt percent, Ni3Al strengthening phase is precipitated during Al aging, the strengthening phase only improves the strength but does not reduce the ductility and toughness,
v, Nb form carbide element strongly, and refined grains are added properly. The carbide is difficult to dissolve, the quenching temperature is increased to coarsen the crystal grains, and V, Nb cannot be too high.
Ti is less than or equal to 0.005 percent, O is less than or equal to 15ppm, N is less than or equal to 20ppm, S is less than or equal to 0.0015 percent, P is less than or equal to 0.005 percent, Ti (CN) is easy to form, the ductility and toughness are reduced, the Ni3Ti needle-shaped precipitation boundary formed by aging improves the strength but reduces the ductility and toughness of the steel, and the oxathion reduces the ductility and toughness of the steel and is strictly controlled.
The first embodiment is as follows:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.037%, Ni: 2.56%, Cr: 12.89%, Mo: 5.19%, W: 1.05%, Co: 11.20%, Al: 0%, Nb: 0.028%, V: 0.116%, Ti: 0.003%, N: 0.0020%, O: 0.0010%, Mn: 0.03%, Si: 0.055%, S: 0.001%, P: 0.005% and the balance of Fe and other inevitable impurity elements.
Example two:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.04%, Ni: 4.00%, Cr: 12.85%, Mo: 5.19%, W: 0.99%, Co: 11.50%, Al: 0%, Nb: 0.03%, V: 0.12%, Ti: 0.002%, N: 0.0016%, O: 0.0008%, Mn: 0.02%, Si: 0.05%, S: 0.001%, P: 0.004%, and the balance of Fe and other inevitable impurity elements.
Example three:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.04%, Ni: 6.10%, Cr: 12.80%, Mo: 5.20%, W: 1.02%, Co: 11.58%, Al: 0.50%, Nb: 0.03%, V: 0.15%, Ti: 0.002%, N: 0.0013%, O: 0.0007%, Mn: 0.02%, Si: 0.04%, S: 0.001%, P: 0.004%, and the balance of Fe and other inevitable impurity elements.
Example four:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.10%, Ni: 8.50%, Cr: 11.50%, Mo: 5.50%, W: 0.80%, Co: 12.02%, Al: 1.00%, Nb: 0.04%, V: 0.13%, Ti: 0.003%, N: 0.0013%, O: 0.0007%, Mn: 0.03%, Si: 0.04%, S: 0.001%, P: 0.004%, and the balance of Fe and other inevitable impurity elements.
Example five:
the corrosion-resistant high-strength stainless steel comprises the following chemical components in percentage by weight:
c: 0.20%, Ni: 12.88%, Cr: 13.30%, Mo: 5.86%, W: 1.21%, Co: 13.21%, Al: 2.00%, Nb: 0.03%, V: 0.14%, Ti: 0.003%, N: 0.0010%, O: 0.0006%, Mn: 0.02%, Si: 0.03%, S: 0.0008%, P: 0.004%, and the balance of Fe and other inevitable impurity elements.
Comparative example one:
the stainless steel comprises the following chemical components:
c: 0.21%, Ni: 5.5%, Cr: 10%, Mo: 2%, W: 1%, Co: 14%, V: 0.3%, and the balance of Fe and other inevitable impurity elements.
Comparative example two:
the stainless steel comprises the following chemical components:
c: 0.08-0.12%, Ni: 2.3-2.7%, Cr: 12-13%, Mo: 4.3-4.7%, W: 0.8-1.2%, Co: 11.5-12.5%, V: 0.2-0.3%, and the balance of Fe and other inevitable impurity elements.
Comparative example three:
the stainless steel comprises the following chemical components:
c: 0.08-0.18%, Ni: 3.00-8.00%, Cr: 3.00-7.00%, Mo: 3.00-6.00%, W: 0.50-2.00%, Co: 10.00-16.00%, V: 0.20-1.00%, and the balance of Fe and other inevitable impurity elements.
The mechanical properties of the examples and comparative examples are compared in the following table:
Figure BDA0003255790640000111
the table shows that the stainless steel of the invention improves the strength of the steel, simultaneously the ductility and toughness are not reduced, the strength grade is 1900-2400MPa, the stainless steel has corrosion resistance, and the service life can be prolonged.
The invention contains Ni, Co, Ni, Co and matrix solid solution to form solid solution strengthening, a highly distorted martensite matrix is obtained by quenching, the martensite matrix precipitates carbides (M2C) after tempering containing strong carbide forming elements W, Mo, Nb, V and Cr, Ni3Al strengthening phase is obtained after tempering containing Al, meanwhile, the ductility and toughness are not reduced, the strength is greatly improved, meanwhile, the invention contains 12-14% of chromium with corrosion resistance, oxygen and nitrogen elements are strictly controlled in the smelting process to avoid forming a plurality of oxides and nitrides, and meanwhile, the nitrogen and oxygen content is controlled to have high corrosion resistance; the invention has another characteristic of high pitting corrosion resistance, which is originated from the chemical composition and the structural uniformity of the material in the metallurgical material, and the addition of W, Mo improves the pitting corrosion resistance of the steel.
The invention also provides a manufacturing method of the corrosion-resistant high-strength stainless steel, and the manufacturing method of the corrosion-resistant high-strength stainless steel comprises the following steps:
according to the chemical composition proportion of stainless steel, vacuum induction smelting is adopted, electrodes are cast, a vacuum consumable remelting steel ingot is subjected to vacuum consumable remelting, steel ingot diffusion annealing, forging, fast forging, cogging, forming and annealing.
Wherein the vacuum induction melting process parameters are as follows:
the furnace burden of the vacuum induction furnace is the furnace burden of pure iron/refined steel materials of metal chromium, nickel, cobalt, molybdenum, tungsten, vanadium, niobium and aluminum with high purity and low sulfur, phosphorus, silicon, manganese, aluminum and titanium; all furnace materials must be clean and dry, have no oil stain and rust and have accurate components.
The good furnace condition is ensured, the furnace is washed by pure iron before the formal smelting, and the electric melting is started under the vacuum degree in the furnace being less than or equal to 2.7 Pa.
And (3) charging sequence: charging a small amount of pure iron-Ni and Co plates-pure iron-metal Mo, W, V and C, feeding power after the Ni and Co plates are charged, charging the rest materials after the Ni and Co plates are slightly red, reserving all Cr and Al during charging, adding fine adjustment components of Cr and Nb after full melting, refining after the Cr and Nb are fully melted, refining for 45 minutes, wherein the temperature in the refining period is 1570-.
The technological parameters of the cast electrode are as follows:
phi 440 and phi 580 electrodes are cast.
And (4) after the electrode is poured, keeping the vacuum state for 40 minutes, then breaking the cavity, carrying out die cooling for 5 hours, demoulding, and carrying out red annealing.
And (3) annealing process of the electrode: as shown in FIG. 1, the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at a speed of less than or equal to 80 ℃/h, the temperature is kept for 20h, and the temperature is gradually decreased to 500 ℃ to be discharged and cooled.
The technological parameters of the vacuum consumable remelting steel ingot are as follows:
the electrode surface is polished without slag lumps, and must be cleaned without rust, oil and dirt.
The consumable crystallizer is phi 508mm and phi 660 mm.
The filling process comprises the following steps: the capping weight is 250-350kg, and the capping time is 60-90 minutes.
And (3) a cooling process: cooling under vacuum for 40min, breaking vacuum, cooling under non-vacuum for 40min, and demolding.
The steel ingot diffusion annealing process parameters are as follows:
as shown in FIG. 2, the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at a speed of less than or equal to 80 ℃/h, the temperature is maintained at the temperature for more than or equal to 25h, and the temperature is gradually decreased to 500 ℃ for discharging and air cooling.
And (4) polishing or polishing the surface of the self-consumption ingot after annealing.
The technological parameters of forging, rapid forging, cogging and forming are as follows:
the heating curve of the steel ingot is as follows:
as shown in figure 3, the steel ingot is kept at the temperature of less than or equal to 600 ℃ for 1h, gradually heated to 900 +/-10 ℃ for more than or equal to 3h, kept at the temperature for 2h, gradually heated to 1250 +/-20 ℃ for more than or equal to 4h, kept at the temperature for more than or equal to 35h, gradually cooled to 1200 +/-10 ℃ and kept at the temperature for more than or equal to 2 h.
According to the characteristic of low heat conductivity coefficient of stainless steel, the raising speed of a steel ingot is slower when the steel ingot is heated, the growing speed of a steel billet is properly increased when the steel billet is heated, but the growing speed cannot be too high, and the steel billet is kept at 900 ℃ for a certain time, so that the heat conductivity and the tissue consistency are improved, and preparation is made for the next step of raising the temperature.
First upsetting and drawing out: tapping the steel ingot, upsetting, drawing down to an intermediate size (the height-diameter ratio is 2.5-2.8) with the reduction of 40-60%; and (4) returning to 1180 +/-10 ℃, and preserving heat for 90-120 minutes.
And (3) upsetting and drawing for the second time: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn to be of an intermediate size (the height-diameter ratio is 2.5-2.8); and (4) returning to 1180 +/-10 ℃, and preserving heat for 90-120 minutes.
Third upsetting and drawing out: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn out to be octagonal with the thickness of 450-490; the furnace is returned to 1050 +/-50 ℃ and the temperature is preserved for 120-150 minutes.
Drawing to phi 300, and final forging temperature is more than or equal to 750 ℃.
After forging, air cooling is carried out until the temperature is less than or equal to 200 ℃, and annealing is carried out in a furnace.
The annealing process comprises the following steps:
as shown in FIG. 4, the temperature is 500 ℃ for 300 plus materials, the temperature is increased to 950 +/-10 ℃ for more than or equal to 6h at the temperature increasing speed of less than or equal to 100 ℃/h, the temperature is maintained at 3h or more, the temperature is reduced to 200 ℃ for remelting, the temperature is gradually increased to 680 ℃ for more than or equal to 630 plus materials, the temperature is maintained at 15h or more, and then the materials are discharged from the furnace for air cooling.
The forging process comprises the following steps:
in order to ensure the forging performance of the steel, the structure of the steel is single-phase austenite during forging, the processing plasticity is good, and the quality of the surface of the steel can be ensured. The steel forging temperature is 1000-. If the finish forging temperature is low, the forging crack is easily generated beyond the optimum thermoplastic region.
Annealing process:
martensitic stainless steels are relatively susceptible to cracking and must be annealed after forging. The steel annealing process of the invention is that after forging, air cooling is carried out until the surface is less than or equal to 200 ℃, and then the steel is fed into a furnace and annealed. The purpose of air cooling for a period of time is to ensure that the internal and external temperatures of the steel are consistent and that the austenite is completely transformed into martensite. In the case of the furnace annealing immediately after forging, untransformed austenite remains in the steel, and the austenite and martensite have different expansion coefficients to generate internal stress, and when the internal stress is higher than the yield strength of the steel, cracks occur in the steel. Normalizing at 950 ℃ to refine grains, controlling the annealing temperature at 630-680 ℃, keeping the temperature for more than or equal to 15h, and discharging and air cooling.
Smelting and casting an phi 580mm electrode bar in a vacuum induction furnace, and remelting a phi 660mm ingot in a vacuum consumable electrode furnace. After the steel ingot is subjected to high-temperature diffusion annealing at 1200-1250 ℃ for more than or equal to 35 hours, the temperature is reduced to 1200-1180 ℃ and the temperature is kept for 1-3 hours, the quick forging machine is subjected to upsetting and drawing out, the steel ingot is subjected to open forging at more than or equal to 1100 ℃, the finish forging temperature is more than or equal to 750 ℃, air cooling is carried out for 8-14 hours after forging, and annealing is carried out at 650 ℃ after air cooling.
The steel bar is subjected to normalizing: air cooling at 1080 ℃; then tempering: air cooling at 650-; quenching: quenching at 1080 ℃, cooling oil to room temperature, and carrying out cryogenic treatment: holding at-73 ℃ for 2 hours, air-cooling to room temperature, tempering: keeping the temperature at 500-550 ℃ for 4-8 hours, and cooling in air for 1-2 times.
Vacuum induction pouring electrode bar, vacuum consumable remelting ingot, forging and cogging, and finished product heat treatment inspection. The method comprises the steps of firstly, controlling ultrahigh purity, smelting by adopting a vacuum induction and vacuum self-consumption double-vacuum process, controlling the content of oxygen and nitrogen at a lower level, and controlling the content of non-metallic inclusions below a level of 1; secondly, high homogenization control is performed, a double-vacuum smelting process is adopted, so that chemical components are uniform, tissues are uniform, and the micro segregation is reduced by high-temperature homogenization diffusion treatment of steel ingots; thirdly, the steel ingot is fine-grained, and the purpose of ultrafine grain is achieved by adopting large deformation amount and multi-directional deformation of the steel ingot and controlling a forging structure.
The implementation principle of the invention is as follows:
the strength of the steel is improved by combining martensite solid solution strengthening, secondary hardening and aging strengthening; w, Al elements are added to improve the yield strength; w, Mo elements are added to improve the pitting corrosion resistance and the high temperature resistance; in order to improve the corrosion resistance, the oxygen and nitrogen content is strictly controlled to improve the purity, and the high purity obviously improves the ductility and toughness of the steel. The vacuum induction furnace and the vacuum consumable electrode furnace are adopted for smelting, the component control accuracy is high, the gas content of steel is effectively reduced by high vacuum degree, and the uniformity of the components of the structure is improved by high cooling speed.
In the description of the present invention, it is to be understood that the terms "center", "longitudinal", "lateral", "length", "width", "thickness", "upper", "lower", "front", "rear", "left", "right", "vertical", "horizontal", "top", "bottom", "inner", "outer", "clockwise", "counterclockwise", and the like, indicate orientations and positional relationships based on those shown in the drawings, and are used only for convenience of description and simplicity of description, and do not indicate or imply that the equipment or element being referred to must have a particular orientation, be constructed and operated in a particular orientation, and thus, should not be considered as limiting the present invention.
Furthermore, the terms "first", "second" and "first" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of the present invention, "a plurality" means two or more unless specifically defined otherwise.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.

Claims (10)

1. The corrosion-resistant high-strength stainless steel is characterized by comprising the following chemical components in percentage by weight:
c: 0.03 to 0.20%, Ni: 2.50-13.00%, Cr: 11.50-13.50%, Mo: 4.00-6.00%, W: 0.50-1.50%, Co: 11.00-13.50%, Al: less than or equal to 2.00 percent, Nb: less than or equal to 0.10 percent, V: less than or equal to 0.25 percent, Ti: less than or equal to 0.005 percent, N: less than or equal to 0.0020 percent, O: less than or equal to 0.0015 percent, Mn: 0.10%, Si: less than or equal to 0.10 percent, S: less than or equal to 0.002%, P: less than or equal to 0.006 percent, and the balance of Fe and other inevitable impurity elements.
2. A method for manufacturing a corrosion-resistant high-strength stainless steel according to claim 1, comprising the steps of:
according to the chemical composition proportion of stainless steel, vacuum induction smelting is adopted, electrodes are cast, a vacuum consumable remelting steel ingot is subjected to vacuum consumable remelting, steel ingot diffusion annealing, forging, fast forging, cogging, forming and annealing.
3. The method for manufacturing the corrosion-resistant high-strength stainless steel according to claim 2, wherein a vacuum induction furnace is used in the vacuum induction melting, and the furnace burden of the vacuum induction furnace is selected from the metals of chromium, nickel, cobalt, molybdenum, tungsten, vanadium, niobium, aluminum and low-sulfur, phosphorus, silicon, manganese, aluminum and titanium pure iron/refined steel burden with high purity.
4. The method of claim 3, wherein the vacuum induction furnace is cleaned with pure iron before the main smelting, and the electric melting is started at a vacuum degree of 2.7Pa or less in the vacuum induction furnace.
5. The method of manufacturing a corrosion-resistant high-strength stainless steel according to claim 4, wherein the vacuum induction melting process parameters are as follows:
and (3) charging sequence: charging a small amount of pure iron-Ni and Co plates-pure iron-metal Mo, W, V and C, feeding power after the Ni and Co plates are charged, charging the rest materials after the Ni and Co plates are slightly red, reserving all Cr and Al during charging, adding fine adjustment components of Cr and Nb after full melting, refining after the Cr and Nb are fully melted, wherein the refining time is more than or equal to 45 minutes, the temperature is controlled to 1570 and 1590 ℃ in the refining period, sampling and analyzing chemical components after refining is finished, adding carbon and aluminum and the like, fully stirring after the carbon and aluminum are fully melted, measuring the temperature, tapping, and controlling the pouring temperature: liquidus +20-70 deg.C;
6. the method of manufacturing a corrosion-resistant high strength stainless steel according to claim 2, wherein the casting electrode process parameters are as follows:
casting phi 440 and phi 580 electrodes;
after the electrode is poured, the vacuum is kept for 40 minutes, then the electrode is broken, and the mold is cooled for 5 hours, demolded and annealed in a red sending way;
and (3) annealing process of the electrode: the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at the speed of less than or equal to 80 ℃/h, the temperature is kept for 20h, the temperature is gradually decreased to 500 ℃, and the mixture is taken out of the furnace for air cooling.
7. The corrosion-resistant high-strength stainless steel and the manufacturing method thereof according to claim 2, wherein the consumable remelting ingot process comprises the following steps:
polishing the surface of the electrode, and cleaning;
phi 508mm and phi 660mm of the consumable crystallizer;
the filling process comprises the following steps: the capping weight is 250-350kg, and the capping time is 60-90 minutes;
and (3) a cooling process: cooling under vacuum for 40min, breaking vacuum, cooling under non-vacuum for 40min, and demolding;
8. the corrosion-resistant high-strength stainless steel and the manufacturing method thereof according to claim 2, wherein steel ingot diffusion annealing process parameters are as follows:
the initial temperature is 350 ℃, the temperature is gradually increased to 630-680 ℃ at the speed of less than or equal to 80 ℃/h, the temperature is maintained at the temperature for more than or equal to 25h, the temperature is gradually decreased to 500 ℃, and the mixture is discharged from the furnace and cooled;
and (4) polishing or polishing the surface of the self-consumption ingot after annealing.
9. The corrosion-resistant high-strength stainless steel and the manufacturing method thereof according to claim 2, wherein the forging, rapid forging, cogging and forming process parameters are as follows:
the heating curve of the steel ingot is as follows: keeping the steel ingot at the temperature of less than or equal to 600 ℃ for 1h, gradually increasing the temperature to 900 +/-10 ℃ within 3h or more, maintaining the temperature for 2h, gradually increasing the temperature to 1250 +/-20 ℃ within 4h or more, maintaining the temperature for 35h or more, gradually decreasing the temperature to 1200 +/-10 ℃ within 2 h;
first upsetting and drawing out: tapping the steel ingot, upsetting, drawing down to an intermediate size (the height-diameter ratio is 2.5-2.8) with the reduction of 40-60%; returning to 1180 +/-10 ℃ and preserving heat for 90-120 minutes;
and (3) upsetting and drawing for the second time: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn to be of an intermediate size (the height-diameter ratio is 2.5-2.8); returning to 1180 +/-10 ℃ and preserving heat for 90-120 minutes;
third upsetting and drawing out: the upsetting reduction of the intermediate billet is 40-60%, and the intermediate billet is drawn out to be octagonal with the thickness of 450-490; the furnace is returned to 1050 +/-50 ℃ and the temperature is preserved for 120-150 minutes;
drawing to phi 300, and the final forging temperature is more than or equal to 750 ℃;
after forging, air cooling is carried out until the temperature is less than or equal to 200 ℃, and annealing is carried out in a furnace.
10. The corrosion-resistant high-strength stainless steel and the manufacturing method thereof according to claim 2, wherein the annealing process parameters are as follows:
when the materials are to be charged, the temperature is between 300 ℃ and 500 ℃, the temperature is increased to 950 +/-10 ℃ within more than or equal to 6 hours at the temperature increasing speed of less than or equal to 100 ℃/h, the temperature is maintained at the temperature for more than or equal to 3 hours, the temperature is cooled to less than or equal to 200 ℃ for remelting, the temperature is gradually increased to 630 ℃ and 680 ℃, the temperature is maintained at the temperature for more than or equal to 15 hours, and then the materials are discharged from the furnace for air cooling.
CN202111059425.6A 2021-09-10 2021-09-10 Corrosion-resistant high-strength stainless steel and manufacturing method thereof Withdrawn CN113930672A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202111059425.6A CN113930672A (en) 2021-09-10 2021-09-10 Corrosion-resistant high-strength stainless steel and manufacturing method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202111059425.6A CN113930672A (en) 2021-09-10 2021-09-10 Corrosion-resistant high-strength stainless steel and manufacturing method thereof

Publications (1)

Publication Number Publication Date
CN113930672A true CN113930672A (en) 2022-01-14

Family

ID=79275526

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202111059425.6A Withdrawn CN113930672A (en) 2021-09-10 2021-09-10 Corrosion-resistant high-strength stainless steel and manufacturing method thereof

Country Status (1)

Country Link
CN (1) CN113930672A (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114990456A (en) * 2022-06-13 2022-09-02 成都先进金属材料产业技术研究院股份有限公司 High-strength and high-toughness stainless steel and ultrahigh-purity and high-structure uniformity control method thereof
CN115369332A (en) * 2022-08-24 2022-11-22 中航上大高温合金材料股份有限公司 Maraging ultrahigh-strength steel and preparation method thereof
CN117230360A (en) * 2023-11-10 2023-12-15 钢铁研究总院有限公司 Preparation method of single-vacuum 300M steel

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114990456A (en) * 2022-06-13 2022-09-02 成都先进金属材料产业技术研究院股份有限公司 High-strength and high-toughness stainless steel and ultrahigh-purity and high-structure uniformity control method thereof
CN114990456B (en) * 2022-06-13 2023-10-13 成都先进金属材料产业技术研究院股份有限公司 High-strength and high-toughness stainless steel and control method for ultrahigh purity and high tissue uniformity of high-strength and high-toughness stainless steel
CN115369332A (en) * 2022-08-24 2022-11-22 中航上大高温合金材料股份有限公司 Maraging ultrahigh-strength steel and preparation method thereof
CN115369332B (en) * 2022-08-24 2023-07-14 中航上大高温合金材料股份有限公司 Maraging ultrahigh-strength steel and preparation method thereof
CN117230360A (en) * 2023-11-10 2023-12-15 钢铁研究总院有限公司 Preparation method of single-vacuum 300M steel
CN117230360B (en) * 2023-11-10 2024-03-05 钢铁研究总院有限公司 Preparation method of single-vacuum 300M steel

Similar Documents

Publication Publication Date Title
WO2021232275A1 (en) Hot-work die steel and preparation method therefor
CN104328353B (en) A kind of rare-earth type 0Cr17Ni4Cu4Nb martensitic precipitations and preparation method thereof
CN111575588B (en) Martensite precipitation hardening stainless steel and preparation method and application thereof
CN107208212B (en) Thick-walled high-toughness high-strength steel plate and method for producing same
CN113930672A (en) Corrosion-resistant high-strength stainless steel and manufacturing method thereof
JP2018525520A (en) Microalloying passenger car carbon hub bearing steel and manufacturing method thereof
CN105525226A (en) Martensitic stainless steel wire rod and production method thereof
CN109112423A (en) Special thick alloy-steel plate of a kind of superior low-temperature toughness and preparation method thereof
CN107130172B (en) 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method
CN112695256A (en) Ferrite martensite steel ladle shell material and preparation method thereof
US20130149188A1 (en) C+n austenitic stainless steel having good low-temperature toughness and a fabrication method thereof
WO2021208181A1 (en) Low-temperature, high-toughness, high-temperature, high-intensity and high-hardenability hot mold steel and preparation method therefor
CN113774280A (en) 2400 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
CN114717488A (en) 1800MPa grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
CN110592491B (en) High-wear-resistance martensite/austenite dual-phase wear-resistant steel plate and manufacturing method thereof
CN114561517A (en) Low-density high-ductility steel and preparation method and application thereof
CN113106356B (en) High-strength martensite precipitation hardening stainless steel and preparation method thereof
CN113699464A (en) Ultra-high-strength high-performance sheet maraging stainless steel and preparation method thereof
CN113667905A (en) Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof
CN113774289A (en) 2700 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof
CN112605557A (en) HGH1131 welding wire and preparation method thereof
CN105568158A (en) Nickel-chromium-free impact-resistant bearing steel and producing method thereof
CN113774270A (en) High-strength high-toughness precipitation hardening stainless steel bar and preparation method thereof
CN114875318B (en) Dispersed delta phase strengthened low-density high-strength and high-toughness steel and manufacturing method thereof
CN114752864B (en) Low-density ultrahigh-strength high-plasticity steel and preparation method and application thereof

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
WW01 Invention patent application withdrawn after publication

Application publication date: 20220114

WW01 Invention patent application withdrawn after publication