CN101403076A - Composite reinforced high-ductility ultrahigh-strength secondary hardening steel - Google Patents
Composite reinforced high-ductility ultrahigh-strength secondary hardening steel Download PDFInfo
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Abstract
The invention belongs to the field of alloy steel, in particular relates to the compound and strengthened secondary hardening steel with high toughness and super-high strength. The steel has the chemical compositions (weight percent) of 0.16-0.26 percent of C, 1.8-2.8 percent of Cr, 10.0-13.0 percent of Ni, 1.0-2.0 percent of Mo, 12.0-15.0 percent of Co, 0.5-1.5 percent of Al, 0.1 percent or less of Mn, 0.1 percent or less of Si, 0.1 percent or less of Ti, 0.005 percent or less of S, 0.008 percent or less of P, 25ppm or less of O, 40ppm or less of N, and the rest of Fe. Compared with the prior art, the secondary hardening steel has better comprehensive performance, more than 2100MPa of tensile strength and favorable plasticity and toughness; more specifically, the tensile strength sigma b is not less than 2100MPa, the reduction of area Psi can reach 55 percent and the rockwell hardness is HRC55.
Description
Technical field
The invention belongs to field of alloy steel, particularly a kind of composite reinforced high-ductility ultrahigh-strength secondary hardening steel.
Technical background
Before this, the secondary hardening type ultrahigh-strength steel of high tenacity is the emphasis of research and application always, and through the development of nearly half a century, it is used more and more widely, wherein representative have HY180, AF1410, an AerMet100 etc., and its chemical ingredients sees Table 1.
The chemical ingredients (wt.%) of the typical secondary hardening type of table 1 ultrahigh-strength steel
| Steel grade | C | Co | Ni | Mo | Cr | Fe |
| HY180 | 0.11 | 8.0 | 10.0 | 1.0 | 2.0 | All the other |
| AF1410 | 0.16 | 14.0 | 10.0 | 1.0 | 2.0 | All the other |
| AerMet100 | 0.23 | 13.4 | 11.1 | 1.2 | 3.1 | All the other |
The intensity of the secondary hardening type ultrahigh-strength steel in the practical application at present all is no more than 2000MPa, and wherein the strength level of AerMet100 steel is the highest, reaches 1965MPa, and the mechanical property of several steel sees Table 2.
The room-temperature mechanical property of the typical Secondery-hardening Ultrahigh Strength Steel of table 2
Though secondary hardening type ultrahigh-strength steel combination of strength and toughness is better, because schedule of reinforcement is single, also there is gap in its maximum intensity with the demand of reality.The development of secondary hardening shaped steel at present mainly relies on single M
2The C alloy carbide is strengthened, and guarantees that material has high tenacity, and its intensity is difficult to surpass 2000MPa.Because its intensity depends critically upon C, Mo in the alloy and the content of Co, develops into AerMet100 from HY180, the C content in the steel brings up to 0.23% by 0.11, but according to studies show that, C content surpasses 0.25% deterioration that can cause fracture toughness property.Therefore continue to rely on M
2C strengthens raising intensity and has arrived the limit substantially, and it is very necessary that the above secondary hardening type ultrahigh-strength steel of 2000MPa is inquired into new schedule of reinforcement.
Summary of the invention
The object of the present invention is to provide a kind of over-all properties good, have the composite reinforced high-ductility ultrahigh-strength secondary hardening steel of above tensile strength of 2100MPa and good plasticity and toughness.
According to above-mentioned purpose, the technical scheme of integral body of the present invention is:
This steel adopts alloy carbide (M
2C) and the mode of intermetallic compound (NiAl) complex intensifying, make it have the ability of superstrength, high-plasticity, high fatigue property.The over-all properties of above tensile strength of 2100MPa and good plasticity and toughness can be provided.
For reaching above-mentioned target, on the alloy ingredient basis of present secondary hardened steel, add alloy element Al and improve Co content, utilize NiAl and M
2The common reinforcement of C reaches high yield strength and tensile strength; The Ni content that improves simultaneously in the steel guarantees enough toughness.
Rest part can comprise that the additional elements of not damaging over-all properties is as uses such as reductors, for example in the alloy: Mn≤0.1%, Si≤0.1%, Ti≤0.1%.P content≤0.008% in the alloy, and S≤0.005%.
According to above-mentioned purpose and whole technical scheme, the concrete technical scheme of the present invention is:
The chemical ingredients of this steel is formed (weight %): C 0.16-0.26%, Cr 1.8-2.8%, Ni 10.0-13.0%, Mo 1.0-2.0%, Co 12.0-15.0%, Al 0.5-1.5%, Mn≤0.1%, Si≤0.1%, Ti≤0.1%, S≤0.005%, P≤0.008%, O≤25ppm, N≤40ppm, surplus is Fe.
Reach the steel of above-mentioned purpose of the present invention and advantage, adopt a kind of secondary hardening type martensitic steel, disperse is separated out on the Fe-Ni martensitic matrix of carbon in the utilization NiAl and M
2C strengthens.
The proportioning of above-mentioned each chemical element is according to as follows:
C: produce the gap solution strengthening, obtain lath martensite, form carbide and increase carbide quantity, reduce the carbonization material dot spacing, increase the secondary hardening peak value, obtain high-yield strength.Studies show that: C content is increased to 0.19% from 0.09%, and the yield strength and the hardness of Fe-10Ni-2Cr-1Mo-8Co steel constantly raise.C content continues to be elevated to 0.29% hardness that still demonstrates under all tempering temperatures and generally raises.Along with the increase of C content, its tensile strength improves, but alloy impelling strength reduces.Too high C content reduces the Ms point, increases residual austenite and twin crystal martensite, and twin crystal martensite damage toughness, too high C content will damage welding property simultaneously.Therefore, for guaranteeing that enough required carbon contents of formation carbide are arranged, form low carbon strip dislocatrion martensite matrix simultaneously, guarantee that steel has satisfied strength level, C content is controlled at 0.16～0.26%.
Cr: improve hardening capacity, produce solution strengthening; Replace M
2Mo among the C forms (Mo, Cr)
2C promotes the secondary hardening reaction, forms the small and dispersed precipitation.The increase of Cr content can be quickened Mo
2The C overaging reduces Mo
2C separates out temperature and returns solubility temperature, improves hardness and yield strength.But along with the continuation of Cr content increases, tensile strength reduces gradually, but it is also relevant with Mo content to improve the effect of impelling strength when being less than 3%Cr.Studies show that of 0.16C-10Ni-14Co alloy: Cr is replaced Mo
2Part Mo among the C is owing to reduced Mo
2Mo content among the C causes Mo
2The C coherency strain reduces, thereby tensile strength, yield strength reduce.If but the corresponding raising of C content but can obtain higher tensile strength and yield strength because of the precipitated phase volume fraction increases.Therefore, according to the C content in the alloy, Cr content is controlled at and is not more than 3.0%.
Mo: as M
2The main forming element of C carbide, intensive produce the secondary hardening reaction, are the reasons that forms the secondary hardening peak, are main strengthening elements, and along with the increase of Mo content, the secondary hardening peak hardness improves, and yield strength improves.For obtaining enough age hardening effect, the Mo content in the steel of the present invention should not be less than 1.0%.Mo increases hardening capacity in addition simultaneously, produces solution strengthening, suppresses the effect of temper brittleness.Mo cooperates with the suitable of Cr, can make alloy obtain good toughness.
Ni: improve hardening capacity, produce solution strengthening, high Ni content guarantees that martensitic matrix has the anti-cleavage fracture ability of high intrinsic, improves the obdurability and the anticorrosion stress-resistant of steel, and Ni can also promote Fe
3C returns molten, thereby is M
2The formation of C provides enough carbon contents, thereby Fe-C-Mo-Cr-Ni-Co adds Ni content 10% or higher in the secondary hardening type ultrahigh-strength steel.And the carbide precipitation that high Ni content and small and dispersed distribute also just this class steel have the fundamental cause of high strength, high tenacity.Among the present invention, alloy Ni in the tempering heat treatment process combines with Al, forms the intermetallic compound precipitation and separates out, and also need consume the Ni content of part, and therefore, control Ni content is not less than 10% in the alloy.
Co: do not form compound with other elements in the alloy system, but promote the secondary hardening reaction strongly, add Co and can suppress to delay the answer of martensite dislocation substructure, keep the high dislocation density of martensite lath, thereby be precipitated phase M subsequently
2Separating out of C provides more nucleation site.And Co improves the intensity of activation of C atom in ferrite, reduces the spread coefficient of C atom in ferrite, increases M
2The nucleation rate of C carbide.Thereby, can promote to form the M that small and dispersed distributes
2The C carbide, and reduce precipitation carbide precipitate spacing of particle; Co can reduce Mo in martensite solid solubility and Cr at M
3Solid solubility in the C cementite, thus M promoted
2The formation of C precipitated phase; Promote that austenite changes martensite fully into, improve the Ms point, reduce martensitic transformation and turn austenitic tendency for reversing.In addition, Ni, Co add jointly and can strengthen promoting Fe mutually
3C returns molten and M
2The formation of C carbide and the promotion sclerization that strengthens Co.
Al: can improve the alloying element that austenitic Ms orders in the common alloying element and have only Co and Al, other alloying element all reduces the Ms point.High CoNi steel alloy is in drawing process, and the intermetallic compound NiAl that Al and Ni can form body-centered cubic structure separates out, and causes coherency strain and produces the reaction of significant secondary hardening, with M
2C forms complex intensifying mutually together.But during the Al too high levels, can make the plasticity and toughness rapid deterioration of alloy, so Al content is difficult for surpassing 1.5% among the present invention.
Other elements in the alloy can comprise the additional elements of not damaging performance.For example, Mn content can reach 0.1%, and preferably less than 0.05%, Si, Ti content all can reach 0.1%, and these additional elements can be used for the reductor of alloy.
All the other elements are iron substantially in the ultrahigh-strength steel of the present invention, and the impurity element in the alloy must be controlled, and for example the P restriction is no more than 0.008%, and the S restriction is no more than 0.005%, and the oxygen restriction is no more than 25ppm, and nitrogen is no more than 40ppm.
The preparation method of employing of the present invention and the close plan of prior art:
Ultrahigh-strength steel of the present invention is easy to adopt vacuum induction+vacuum consumable remelting or vacuum induction+electric slag refusion and smelting technology, and its concrete processing parameter is as follows:
Steel ingot carries out 1200+10 ℃ of homogenizing to be handled, time 〉=3 hour.Charging temperature≤650 ℃.
Alloy all can hot-work in 1180-850 ℃ of interval, Heating temperature: 1160-1180 ℃, opens forging temperature 〉=1100 ℃, final forging temperature 〉=850 ℃.
Finished products system: normalizing: 950 ± 15 ℃, be incubated 〉=1 hour; Tempering: 680 ± 20 ℃, be incubated 〉=6 hours.
Final thermal treatment: quench treatment: be heated to 910 ± 15 ℃, insulation is 1 hour behind the heat penetration, oil quenching.Also allow air cooling or carry out vacuum heat treatment with rare gas element, the two is slower than oil quenching rate of cooling.Carry out sub-zero treatment subsequently, in air, be raised to room temperature in 〉=1 hour then-73 ℃ of insulations.
Temper: be heated to 510 ± 10 ℃, insulation is 5-8 hour behind the heat penetration, air cooling.Also can carry out double tempering handles.
Compared with prior art, high comprehensive performance of the present invention has the advantage of above tensile strength of 2100MPa and good plasticity and toughness.Have higher specific tenacity simultaneously, its specific tenacity is not less than the Ti-6Al-4V titanium alloy, can substitute existing ultrahigh-strength steel under the working conditions that requires higher combination of strength and toughness and weight reduction.
Steel of the present invention can provide ultimate tensile strength to be not less than 2100MPa after austenitizing and timeliness, and relative reduction in area ψ can reach 55%, and usefulness provides Rockwell hardness HRC55 during with above-mentioned working procedure parameter, has good combination of strength and toughness.
Embodiment
The chemical ingredients scope of steel according to the present invention adopts 25 kilograms of vacuum induction furnaces to prepare 21 kilograms alloy pig 8 stoves, and its concrete chemical ingredients sees Table 3, and heat (batch) number is 1
#～8
#
After 8 stove smelting steels are cast into steel ingot, at first carry out high temperature homogenization processing system before the forging and be: 1200 ℃ of insulations are after 6 hours, and cooling is forged, and the Forge Heating temperature is 1150 ℃.The forging coupon is of a size of: φ 15 * 2000mm, 15 * 15 * 2000mm and 25 * 45 * L.
Forge the back coupon and at first carry out normalizing, annealing thermal treatment: 950 ℃ * 1h of normalizing treatment, air cooling, 680 ℃ * 6h of anneal, air cooling.Send the processing of sample section stretching, impact and fracture toughness specimen blank then.Last thermal treatment is quenched, deep cooling and tempering heat treatment: 910 ℃ * 1h of quench treatment, oil quenching, ℃ deepfreeze subsequently-73 are raised to room temperature in the air.510 ℃ * 5h of temper, air cooling.The ground finish of sample blank becomes mechanical property sample finished product, records mechanical property and sees Table 4.
In order to contrast, in table 3 and table 4, listed the chemical ingredients and the mechanical property of AerMet100, AF1410 steel in.
Table 3 is found out, compares with AerMet100, these secondary hardening type ultrahigh-strength steel of AF1410 steel, and main technical schemes of the present invention is on the martensitic matrix of middle carbon, by compound interpolation Mo, Cr, Al, utilizes M
2The common reinforcement of C type carbide and intermetallic compound NiAl reaches high strength; Higher Co content can improve the Ms point, helps the formation of lath martensite, more can slow down the recovery of dislocation, promotes separating out of strengthening phase, helps improving intensity; Higher Ni content improves the hardening capacity of steel, can obtain the toughness that enough austenites improve steel especially.
Find out that by table 4 steel of the present invention is compared with comparative example A erMet100, AF1410 steel,, can reach more than the 2100MPa keeping higher plasticity and toughness to have higher tensile strength simultaneously.
Claims (1)
1, a kind of composite reinforced high-ductility ultrahigh-strength secondary hardening steel is characterized in that the chemical ingredients composition (weight %) of this steel is: C 0.16-0.26%, Cr 1.8-2.8%, Ni 10.0-13.0%, Mo 1.0-2.0%, Co 12.0-15.0%, Al 0.5-1.5%, Mn≤0.1%, Si≤0.1%, Ti≤0.1%, S≤0.005%, P≤0.008%, O≤25ppm, N≤40ppm, surplus is Fe.
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| CN102031459A (en) * | 2010-12-28 | 2011-04-27 | 钢铁研究总院 | W-containing high-strength and high-toughness secondary hardening stainless steel |
| CN102226253A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | Carburized bearing steel for high-speed railways and preparation method thereof |
| CN102226252A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof |
| CN104948765A (en) * | 2015-07-13 | 2015-09-30 | 苏州工业园区思达德阀门有限公司 | Cryogenic ball valve |
| CN105177455A (en) * | 2015-10-08 | 2015-12-23 | 中国航空工业集团公司北京航空材料研究院 | 2400MPa-grade high-alloy ultrahigh-strength steel |
| CN106167850A (en) * | 2016-08-30 | 2016-11-30 | 陕西千山航空电子有限责任公司 | A kind of 23Co14ni12cr3mo Heat-Treatment of Steel method |
| CN106755773A (en) * | 2016-12-02 | 2017-05-31 | 哈尔滨东安发动机（集团）有限公司 | The softening method of carburized zone after a kind of CSS 42L pinion steel carburizings |
| CN112981275A (en) * | 2019-12-17 | 2021-06-18 | 上海大学 | Composite precipitation strengthening steel with strength of 2200MPa or above and manufacturing method thereof |
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| CN102031459A (en) * | 2010-12-28 | 2011-04-27 | 钢铁研究总院 | W-containing high-strength and high-toughness secondary hardening stainless steel |
| CN102226253A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | Carburized bearing steel for high-speed railways and preparation method thereof |
| CN102226252A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof |
| CN102226253B (en) * | 2011-06-10 | 2013-03-20 | 钢铁研究总院 | Carburized bearing steel for high-speed railways and preparation method thereof |
| CN102226252B (en) * | 2011-06-10 | 2013-03-20 | 钢铁研究总院 | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof |
| CN104948765A (en) * | 2015-07-13 | 2015-09-30 | 苏州工业园区思达德阀门有限公司 | Cryogenic ball valve |
| CN104948765B (en) * | 2015-07-13 | 2016-08-24 | 苏州工业园区思达德阀门有限公司 | Cryogenic ball valve |
| CN105177455A (en) * | 2015-10-08 | 2015-12-23 | 中国航空工业集团公司北京航空材料研究院 | 2400MPa-grade high-alloy ultrahigh-strength steel |
| CN106167850A (en) * | 2016-08-30 | 2016-11-30 | 陕西千山航空电子有限责任公司 | A kind of 23Co14ni12cr3mo Heat-Treatment of Steel method |
| CN106755773A (en) * | 2016-12-02 | 2017-05-31 | 哈尔滨东安发动机（集团）有限公司 | The softening method of carburized zone after a kind of CSS 42L pinion steel carburizings |
| CN112981275A (en) * | 2019-12-17 | 2021-06-18 | 上海大学 | Composite precipitation strengthening steel with strength of 2200MPa or above and manufacturing method thereof |
| CN112981275B (en) * | 2019-12-17 | 2022-06-14 | 上海大学 | Composite precipitation strengthening steel with strength of 2200MPa or above and manufacturing method thereof |
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