CN106048435A - High-hardenability low-yield-ratio alloy steel and preparation method - Google Patents

High-hardenability low-yield-ratio alloy steel and preparation method Download PDF

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CN106048435A
CN106048435A CN201610065359.6A CN201610065359A CN106048435A CN 106048435 A CN106048435 A CN 106048435A CN 201610065359 A CN201610065359 A CN 201610065359A CN 106048435 A CN106048435 A CN 106048435A
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steel
hour
temperature
yield
low
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刘少尊
王春旭
厉勇
黄顺喆
韩顺
刘宪民
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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 provides high-hardenability low-yield-ratio ultrahigh-strength steel and a preparation method and belongs to the technical field of alloy steel. The steel comprises, by weight, 0.33%-0.43% of C, 0.50%-3.5% of Cr, 2.0%-6.0% of Ni, 0.5%-1.50% of Si, 0.5%-1.50% of Mn, 0.5%-2.0% of Mo, 0-0.3% of V, 0-0.2% of Nb and the balance Fe and other inevitable impurity elements. Compared with the prior art, the high-hardenability low-yield-ratio ultrahigh-strength steel has the advantages that the steel is excellent in comprehensive performance, can be subjected to air-cooling quenching to obtain complete martensite capacity, and has the high tenacity sigma b of 1900 MPa or over and the ultrahigh strength K<IC> of 90 MPam<1/2> or over, and meanwhile, the steel has the yield ratio below 0.80 and has excellent toughness, adiabatic shearing resistance, heat treatment manufacturability and economical efficiency.

Description

A kind of high-hardenability low yield strength ratio steel alloy and preparation method
Technical field
The invention belongs to technical field of alloy steel, particularly to a kind of high-hardenability low yield strength ratio (σ0.2/σb≤ 0.8) super High strength steel and preparation method, have excellent obdurability (σb>=1900MPa, KIC≥90MPam1/2), excellent anti-Adiabatic Shear Ability, good Technology for Heating Processing and economy.
Background technology
Before this, due to the advantage of economy, low-alloy super-strength steel is always the main force of unimach application, It is widely used in the industries such as Aeronautics and Astronautics, machinery, traffic, mainly has 30CrMnSi, 30CrMnSiNi2, D406A, D6AC etc., But the intensity of these low-alloy super-strength steels is generally at below 1800MPa, and the intensity such as 300M steel of higher intensity rank can To reach 2000MPa level, but fracture toughness is relatively low, at 70MPam1/2Below.
With the development of aerospace industries, the design and select material demand for high tenacity high reliability is the most prominent, has While high intensity, need that there is high tenacity, adapt to shock loading or the ability of cyclic loading, it is desirable to tensile strength sigma simultaneouslyb≥ 1900Mpa has K simultaneouslyIC≥90MPam1/2High tenacity.Under shock loading condition uses, it is desirable to there is relatively low bending by force Ratio, yield tensile ratio is below 0.8.
Increase recently as parts shape complexity, it is desirable to material has bigger quenching degree, utilize air quenching to meet Complicated quenching degree and the conforming demand of structure property.The quenching degree of steel alloy is had higher requirement.Although it is current Low-alloy steel can provide σb>=1620MPa, KIC≥80MPam1/2Performance, but with current field of aerospace for zero The demand of part is compared, and the combination property of intensity and fracture toughness etc. remains in gap, and intensity and toughness are the most on the low side, it is impossible to meet skill Art demand.The most above-mentioned steel all uses oil quenching technique, it is desirable to part can use air quenching to get final product the quenching intensity of through hardening, meets Complex parts requirement.Want to develop a kind of price economy, intensity stabilization at more than 1900MPa, be provided simultaneously with excellent anti- Low stress damage ability, i.e. fracture toughness KIC≥90MPam1/2Unimach, there is the yield tensile ratio of less than 0.8, have excellent Different obdurability, Technology for Heating Processing and economy.
Under the conditions of high strain-rate, adiabatic shear fracture is the failure mode that material is universal.Material is at High speed load During, strain rate is up to 103～106s-1, the time of whole deformation process is extremely short, plastic deformation the heat produced comes not And scatter away, it is believed that it is " adiabatic " process.There is the biggest difference in the complexity of different materials generation adiabatic shear Not, the Adiabatic Shear characteristic of material directly affects the high strain-rate serviceability of material.Material is made Φ 4 × 4mm sample, profit Carry out forced shear test with split hopkinson press bar, test the ultimate deformation speed that material can bear, can be the most anti- (ultimate deformation speed is the highest, and anti-Adiabatic Shear ability is the strongest, and i.e. Adiabatic Shearing Sensitivity is more to reflect the anti-Adiabatic Shear ability of material Low).
Therefore, a new generation has the low-alloy super-strength steel day of high-hardenability, low yield strength ratio, low Adiabatic Shearing Sensitivity Come in the referred scientific research schedule of benefit.
The low-alloy super-strength steel composition of at present typical case's application and mechanical property are shown in Tables 1 and 2:
Table 1 compared steel chemical composition (wt%)
Table 2 compared steel mechanical property
Summary of the invention
It is an object of the invention to provide the superhigh intensity that a kind of high-hardenability low yield strength ratio anti-Adiabatic Shear ability is good Steel and preparation method, be a kind of economical unimach of high-hardenability low yield strength ratio, and high comprehensive performance has air quenching permissible Obtain complete martensite ability, σb>=1900MPa and KIC≥90MPam1/2High tenacity and superhigh intensity while, have 0.8 Following yield tensile ratio, has obdurability, anti-Adiabatic Shear ability, Technology for Heating Processing and the economy of excellence.
Based on above-mentioned purpose, the main technical schemes of the present invention is on the basis of middle carbon lonneal martensite steel, higher Cr, Ni content make C curve move to right raising quenching degree, the interpolation strictly controlling Si, Mn can obtain relatively low yield tensile ratio, Cr, Ni The cooperation of content controls Ms point, adds Mo, Nb, V, alloy lonneal martensite steel in formation.Its concrete chemical composition becomes Point (weight %) is: C0.33-0.43%, Cr0.50-3.5%, Ni2.0-6.0%, Si0.5-1.50%, Mn0.5-1.50%, Mo0.5-2.0%, V0-0.3%, Nb0-0.2%, remaining is Fe and other inevitable impurity elements.
The design considerations of above-mentioned chemical composition is as follows:
C: quench, be tempered after in order to obtain required high intensity, its tensile strength is in linear relation with C content:
σb(MPa)=(294 × C%+82) × 9.8
In formula, C% represents carbon content in steel, and the scope of application is 0.30～0.50%C.For reaching the strong of more than 1900MPa Degree, C content must more than 0.33%, but too much C content can the plasticity and toughness of severe exacerbation steel and the processing performance of steel, simultaneously The anti-Adiabatic Shear ability of serious infringement, thus C content controls as 0.33-0.43%.
Cr: quenching degree and the resistance to tempering of steel can be effectively improved, the high intensity needed for obtaining, significantly improve simultaneously Anti-decarburization capacity, but too high levels then can significantly improve the hardening heat of steel, the toughness reducing steel and processability, and also same with Ni Shi Tianjia can significantly reduce Ms point.In the present invention, Cr content should be the highest about 3.0%, therefore controls at 0.5-3.5%.
Ni: be effectively improved the quenching degree of steel and improve the low-temperature flexibility of steel.Reduce Ms point, it is possible to obtain remaining difficult to understand simultaneously Family name's body, improves the toughness of steel, reaches about 3.0% and substantially postpone C curve, significantly improve quenching degree, be the main of steel of the present invention One of technical measures, but too high Ni content more than 6% time due to Ms point too low, can not get complete martensitic structure, remaining difficult to understand Family name's body too much reduces intensity, it is necessary to uses subzero treatment to make Technology for Heating Processing complicated, therefore controls at 2.0-6.0%.
Si: add Si in steel, retained austenite can be suppressed to Fe3The decomposition of C changes, and makes Temper Martensite Embrittlement district Move to high temperature direction, reduce one-step temper embrittlement, high-temperature tempering process therefore can be used to obtain good obdurability Proportioning, but high Si can reduce anti-decarbonization performance, significantly improves yield strength and yield tensile ratio, for reaching in drawing process simultaneously The yield tensile ratio of less than 0.80, in steel of the present invention, Si controls below 1.5%.
Mn: quenching degree and the intensity of steel can be improved, but during Mn too high levels, have the tendency making crystalline grain of steel be roughened, and increase Add the crisp sensitivity of steel belt roof bolt, increase component segregation in vacuum consumable remelting metallurgical process simultaneously, and Mn Yu Si improves surrender Intensity and yield tensile ratio, thus control Mn content 0.5-1.50%.
Mo: while being effectively improved quenching degree and the resistance to tempering of steel, additionally it is possible to strengthening crystal boundary.Content is less than 0.20% Being difficult to function as described above, but content is markedly improved over 950 DEG C more than 2.0% solid solubility temperature, roughening tissue reduction is moulded tough Property, therefore Mo content controls at 0.5-2.0%.
V: carry out complex intensifying by the MC type precipitated phase of formation small and dispersed in low-alloy super-strength steel, improve steel Intensity and toughness.V content is difficult to function as described above less than 0.05%, and too high V can reduce plasticity, controls at 0-0.3%.
Nb: crystal grain thinning, improves the toughness of steel, and content does not has above-mentioned effect less than 0.01%, can increase more than 0.3% Fragility is inclined to, and the present invention controls less than 0.2%.
High impact toughness unimach of the present invention is prone to use vacuum induction+vacuum consumable remelting or electroslag remelting work Skill, it is possible to use external refining+vacuum consumable remelting or electroslag remelting process, the technical parameter controlled in technique is as follows:
Steel ingot carries out 1190-1230 DEG C of Homogenization Treatments, 8 hours≤diffusion time≤60 hour, charging temperature≤650 ℃；
Heating-up temperature: 1160-1180 DEG C, 1100 DEG C≤open forging temperature≤1160 DEG C, 800 DEG C≤final forging temperature≤900 DEG C；
Finished products system: normalizing: 910-950 DEG C, 1 hour≤temperature retention time≤3 hour air cooling；Annealing: 640-700 DEG C, 6 hours≤temperature retention time≤30 hour.
Finished heat treatment: Quenching Treatment: be heated to 880-950 DEG C, is incubated 1-3 hour after heat penetration, air cooling, air-cooled or oily Quench；
Temper: be heated to 230-280 DEG C, is incubated 2-4 hour after heat penetration, air cooling；Or carry out double tempering process.
According to the steel of the present invention prepared by above-mentioned chemical composition and production method, there is air quenching and can obtain complete martensite Ability, σb>=1900Mpa and KIC≥90MPam1/2High tenacity and superhigh intensity while, there is the yield tensile ratio of less than 0.8, 3600-4300s-1Limiting strain speed.There is obdurability, anti-Adiabatic Shear ability, Technology for Heating Processing and the economy of excellence Property.
Compared with prior art, high comprehensive performance of the present invention, there is higher intensity and fracture toughness, have good resisting Adiabatic Shear ability, has good quenching degree and Technology for Heating Processing simultaneously.
Detailed description of the invention
According to the chemical composition ranges of the economical high tenacity of the present invention easy spinning easy-welding super strong steel, use 25 kilograms Alloy pig 10 stove of 20 kilograms prepared by vaccum sensitive stove, and its specific chemical composition is shown in Table 3.
After test steel smelting is cast into steel ingot, first carrying out high temperature homogenization resolving system before forging is: 1200 DEG C of insulations 10 After hour, cooling forging, Forge Heating temperature is 1150 DEG C.Forging coupon is a size of: φ 15 × 2000mm, 15 × 15 × 2000mm and 25 × 45 × Lmm.
After forging coupon first carry out normalizing, annealing heat treatment: 950 DEG C × 1h of normalized treatment, air cooling, annealing 680 DEG C × 5h, air cooling.Then the processing stretching of sample section, impact and fracture toughness specimen blank are sent.Finally carry out quenching, being tempered at heat Reason: 930 DEG C × 1h of Quenching Treatment, air cooling；260 DEG C × 3h of temper, AC.Mechanics can be tested after sample blank grinding Performance is shown in Table 2.
In order to contrast, Tables 1 and 2 listed in comparative example low-alloy super-strength 30CrMnSiNi2A, 406, D406A steel Chemical composition and mechanical property.
As seen from Table 3, with comparative example low-alloy 30CrMnSiNi2A, 406, compared with D406A steel, the major technique of the present invention Scheme is to significantly improve the content of C and Ni, reduces Si content, adds higher Mo, Nb, V simultaneously, and in formation, low-alloy low temperature returns Fire martensite steel.Higher C content improves intensity；Higher Ni content improves the quenching degree of steel and obtains enough remaining Austria Family name's body improves impact flexibility, reduces yield tensile ratio simultaneously；Strict Si, Mn content controlled meets low yield strength ratio needs.
Being found out by table 4, steel grade of the present invention is compared with comparative example, and tensile strength and fracture toughness, higher than the latter, have stable σb>=1900MPa tensile strength and KIC≥90MPam1/2Fracture toughness, there is good quenching degree and low yield strength ratio simultaneously, Air quenching i.e. can be with through hardening.
Being found out by table 5, steel grade of the present invention is compared with comparative example, under high strain rate, after anti-Adiabatic Shear ability is higher than Person, has 3800-4200s-1Limiting strain speed, meanwhile, uniform plastic strain, impact absorbing can be above 300M steel.
Table 3 embodiment of the present invention contrasts table with comparative example chemical composition (wt%)
Table 4 embodiment of the present invention contrasts table with comparative example mechanical property
Table 5 embodiment of the present invention contrasts table with comparative example mechanical property

Claims (2)

1. a high-hardenability low yield strength ratio unimach, it is characterised in that chemical composition weight % is: C 0.33- 0.43%, Cr 0.50-3.5%, Ni 2.0-6.0%, Si 0.5-1.50%, Mn 0.5-1.50%, Mo 0.5-2.0%, V 0-0.3%, Nb 0-0.2%, remaining is Fe and other inevitable impurity elements.
2. a preparation method for a kind of high-hardenability low yield strength ratio unimach described in claim 1, uses vacuum sense Should+vacuum consumable remelting or electroslag remelting, or use external refining+vacuum consumable remelting or electric slag refusion and smelting technique；It is special Levying and be, the technical parameter controlled in technique is as follows:
Steel ingot carries out 1180-1230 DEG C of Homogenization Treatments, 8 hours≤diffusion time≤60 hour, charging temperature≤650 DEG C；
Heating-up temperature: 1150-1180 DEG C, 1100 DEG C≤open forging temperature≤1160 DEG C, 800 DEG C≤final forging temperature≤900 DEG C；
Finished products system: normalizing: 910-930 DEG C, 1 hour≤temperature retention time≤3 hour air cooling；Tempering: 640-700 DEG C, 6 is little Time≤temperature retention time≤30 hour；
Finished heat treatment: Quenching Treatment: be heated to 860-930 DEG C, is incubated 1-3 hour after heat penetration, air cooling, air-cooled or oil quenching；
Temper: be heated to 230-280 DEG C, is incubated 2-6 hour after heat penetration, air cooling；Or carry out double tempering process.
CN201610065359.6A 2016-02-01 2016-02-01 High-hardenability low-yield-ratio alloy steel and preparation method Pending CN106048435A (en)

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108179359A (en) * 2018-02-27 2018-06-19 苏州特鑫精密电子有限公司 A kind of heat treatment process of high intensity hardware shrapnel
CN110306127A (en) * 2019-07-11 2019-10-08 上海交通大学 A kind of ultrahigh-intensity high-toughness steel alloy and preparation method thereof
CN112143960A (en) * 2019-06-28 2020-12-29 宝山钢铁股份有限公司 Steel plate with ultrahigh strength and low yield ratio and manufacturing method thereof
CN115094337A (en) * 2022-07-22 2022-09-23 上海大学(浙江)高端装备基础件材料研究院 Ultrahigh-strength alloy steel, 19.8-grade threaded fastener and preparation method thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000160282A (en) * 1998-11-26 2000-06-13 Nkk Corp Bainitic rail excellent in wear resistance and flaking resistance
JP2001049398A (en) * 1999-08-06 2001-02-20 Toshiba Corp High toughness heat resistant steel, and manufacture of turbine rotor
CN102212760A (en) * 2011-06-10 2011-10-12 钢铁研究总院 Steel with high toughness and ultrahigh strength
CN104328359A (en) * 2014-11-04 2015-02-04 钢铁研究总院 High-toughness ultrahigh-strength D506A steel easy for rotary extrusion and easy to weld and preparation method thereof

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000160282A (en) * 1998-11-26 2000-06-13 Nkk Corp Bainitic rail excellent in wear resistance and flaking resistance
JP2001049398A (en) * 1999-08-06 2001-02-20 Toshiba Corp High toughness heat resistant steel, and manufacture of turbine rotor
CN102212760A (en) * 2011-06-10 2011-10-12 钢铁研究总院 Steel with high toughness and ultrahigh strength
CN104328359A (en) * 2014-11-04 2015-02-04 钢铁研究总院 High-toughness ultrahigh-strength D506A steel easy for rotary extrusion and easy to weld and preparation method thereof

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108179359A (en) * 2018-02-27 2018-06-19 苏州特鑫精密电子有限公司 A kind of heat treatment process of high intensity hardware shrapnel
CN112143960A (en) * 2019-06-28 2020-12-29 宝山钢铁股份有限公司 Steel plate with ultrahigh strength and low yield ratio and manufacturing method thereof
CN110306127A (en) * 2019-07-11 2019-10-08 上海交通大学 A kind of ultrahigh-intensity high-toughness steel alloy and preparation method thereof
CN110306127B (en) * 2019-07-11 2021-12-17 上海交通大学 Ultrahigh-strength high-toughness alloy steel and preparation method thereof
CN115094337A (en) * 2022-07-22 2022-09-23 上海大学(浙江)高端装备基础件材料研究院 Ultrahigh-strength alloy steel, 19.8-grade threaded fastener and preparation method thereof

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