CN102747303B - High-strength steel sheet with yield strength of 1100MPa and manufacturing method thereof - Google Patents
High-strength steel sheet with yield strength of 1100MPa and manufacturing method thereof Download PDFInfo
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Abstract
A high-strength steel sheet with yield strength of 1100MPa and a manufacturing method thereof. The high-strength steel sheet comprises, based on the weight percentage, 0.15-0.25% of C, 0.10-0.50% of Si, 0.60-1.20% of Mn, no more than 0.013% of P, no more than 0.003% of S, 0.20-0.55% of Cr, 0.20-0.70% of Mo, 0.60-2% of Ni, 0-0.07% of Nb, 0-0.07% of V, 0.0006-0.0025% of B, 0.01-0.08% of Al, 0.003-0.06% of Ti, no more than 0.00018% of H, no more than 0.0040% of N, no more than 0.0030% of O, and the balance of Fe and inevitable impurities; and the carbon equivalent CEQ is no more than 0.60%. A quenching and a tempering heat treatment are employed to obtain a tempered martensite tissue. The steel provided by the present invention has yield strength no less than 1100MPa, tensile strength no less than 1250MPa, Charpy ballistic work Akv (-40 DEG C) no less than 50J, and good strength and toughness.
Description
Technical field
The present invention relates to the ultrahigh-strength steel plates with good low-temperature toughness, be specifically related to yield strength 1100MPa grade high-strength steel plate and manufacture method thereof.
Background technology
High tensile steel plate application and coal mine machinery are if coal mine hydraulic supporting etc., engineering machinery are as equipments such as crawler mounted crane, crane and truck mounted concrete pump etc. and large-scale floating cranes peculiar to vessel.Physical construction is on active service usually in large load and complex environment, and therefore physical construction high tensile steel plate requires that steel plate has higher intensity and good low-temperature flexibility.The high tensile steel plate that current Europe superscript EN10025 and GB 16270 relate to, its yield strength is up to 960MPa.Current ultra-large type engineering machinery, as large-tonnage crawler mounted crane and crane etc., all needs to use yield strength 1100MPa level steel plate.
Choose suitable chemical composition, in conjunction with the controlled rolling and controlled cooling optimized or Q-tempering technique, the high tensile steel plate meeting machinofacture customer need can be produced.Adopt controlled rolling and controlled cooling mode to produce high tensile steel plate, in rolling and process of cooling, control difficulty comparatively large, affect the overall homogeneity of mechanical property of steel plate.Adopt Q-tempering explained hereafter high tensile steel plate, improved the hardening capacity of steel plate by the content of alloying element and carbon, make steel plate form martensitic stucture in process of cooling.Martensite is that carbon is solid-solubilized in iron atom body centered structure, makes the tetragonal lattice that bcc lattice extends to form along c-axis direction, and this type of tissue has higher intensity and hardness.Martensite is formed in trimming phase transformation mode, and the forward position of phase transformation is a row glissile dislocation, and trimming can cause surface relief effect, causes martensitic stucture to strain energy storage comparatively large, reach 1000J/mol even higher by crystal trimming.The martensitic stucture that trimming is formed is tiny, and between martensite lamella, defect concentration is larger.Larger defect concentration is that tiny crack shape closes source of growing up, and can form tiny crack under stressed effect, tiny crack is grown up and made steel plate and rupture rapidly along crystal boundary, and the low-temperature impact work therefore with the high tensile steel plate of martensitic stucture is lower.Therefore, need by optimizing composition and technique, exploitation has the high tensile steel plate of good obdurability coupling.
Summary of the invention
The object of the present invention is to provide a kind of yield strength 1100MPa grade super strength steel plate and manufacture method thereof, adopt quenching-and-tempering process, yield strength reaches the ultrahigh-strength steel plates of 1100MPa level, and this steel plate has good low-temperature flexibility.
For achieving the above object, technical scheme of the present invention is:
A kind of yield strength 1100MPa grade high-strength steel plate, its chemical component weight per-cent is:
C：0.15~0.25%
Si：0.10~0.50%
Mn：0.60~1.20%
P：≤0.013%
S：≤0.003%
Cr：0.20~0.55%
Mo：0.20~0.70%
Ni：0.60~2.00%
Nb：0~0.07%
V：0~0.07%
B：0.0006~0.0025%
Al：0.01~0.08%
Ti：0.003~0.06%
H：≤0.00018%
N≤0.0040%
O≤0.0030%
All the other are Fe and inevitable impurity,
And, carbon equivalent ce Q≤0.60%; Obtain tempered martensite, the yield strength >=1100MPa of steel plate, tensile strength >=1250MPa, Xia Shi Impact energy Ak v(-40 DEG C) >=50J.
In present component design:
C:C doses in steel, improves the hardening capacity of steel plate, makes steel plate in quench cooled process, form the higher martensitic stucture of hardness.C content improves, then martensite hardness increases, and correspondingly the intensity of steel plate increases, but toughness can be caused to decline.C content increases, and the welding property of steel plate can be caused to be deteriorated, comprehensive obdurability and welding property, and in patent of the present invention, setting carbon content is 0.15 ~ 0.25%.
Si:Si substitutes Fe atom with substitute mode in steel, hinders dislocation motion, improves the strength property of steel plate.Si can reduce C in ferritic middle diffusibility, and therefore appropriate when tempering Si can avoid the formation of thick carbide and separate out at fault location.The higher welding property that can worsen steel plate of Si content.Therefore the Si content in steel plate the present invention is controlled as Si:0.10 ~ 0.50%.
Mn:Mn is weak carbide forming element, and the Mn in steel mainly exists with solution.Steel plate is in quenching process, and Mn can suppress diffusion transformation, improves the hardening capacity of steel plate, forms the martensitic stucture of refinement, and this class loading has good obdurability coupling.The higher meeting of Mn content causes there is Mn segregation in steel plate, worsens steel plate interior tissue, may form larger MnS simultaneously and be mingled with, cause UT (Ultrasonic Testing) not conform to.Add the Mn of 0.60 ~ 1.20% in the present invention, be conducive to the hardening capacity improving steel plate, and reduce the impact of center segregation on steel plate.
P: in steel, P is at Grain Boundary Segregation, can reduce crystal boundary in conjunction with energy, reduce the low temperature impact properties of steel plate.P and Mn exists jointly can aggravate steel belt roof bolt fragility.There is grain boundary fracture when the P of Grain Boundary Segregation can make steel plate in the effect being subject to shock load, form larger cleavage surface, reducing the energy that steel plate absorbs when being subject to impacting.P can worsen the welding property of steel, therefore for welding, needs as far as possible low P content to ensure weldability.Add the P being no more than 0.013% in the present invention, ensure that ultrahigh-strength steel plates has good low temperature impact properties.
The solubleness of S:S in delta ferrite and austenite is very little, and in solidification of molten steel process, S segregation can occur, and forms more sulfide inclusion, the UT (Ultrasonic Testing) performance of harm steel plate and low temperature impact properties.In welding process, S easily causes thermal crack, simultaneously because S is oxidizable, generates SO
2gas is overflowed, and produces pore and loosen in welding metal.Add the S being no more than 0.003% in the present invention, ensure that steel plate has good low temperature impact properties and obdurability coupling.
Cr:Cr doses in steel, can suppress the diffusion transformation of steel plate, improves the hardening capacity of steel plate, forms the martensitic stucture of sclerosis, obtains the steel plate with higher-strength.Cr too high levels, can cause the welding property of steel plate to reduce, therefore add the Cr of 0.20 ~ 0.55% in the present invention, ensures intensity and the welding property of steel plate.
Mo:Mo can improve the hardening capacity of steel plate, makes steel plate form martensite in quenching process.If quenching velocity is very fast, and in lower temperature range tempering, then Mo is mainly present in steel with solution, plays solid solution strengthening effect.The Mo of certain content is dosed in steel, can improve the intensity of steel plate, and the low temperature impact properties of steel plate can not be worsened, but higher Mo can worsen Plate Welding performance, therefore the Mo of 0.20-0.70% is added in patent of the present invention, to obtain the coupling of obdurability and welding property.
Nb:Nb adds in steel, plays the restraining effect to steel plate recrystallization, makes steel plate at lesser temps recrystallize, refine austenite, thus reaches the object that refinement finally organizes.Nb content is higher, can form thicker NbC particle, cause the low temperature impact properties of steel plate to worsen at grain boundaries.Coordinate other alloying element, add the Nb of 0 ~ 0.07% in the present invention to ensure the mechanical property of steel plate.
Ni:Ni exists with solution in steel, and in component system of the present invention, Ni exists with the FCC phase of Fe-Ni-Mn, reduces stacking fault energy, improves the low temperature impact properties of steel plate.Ni belongs to noble metal, and higher Ni content can cause Plate Production cost to increase, and therefore adds the Ni of 0.60 ~ 2.00% in the present invention to ensure the mechanical property of steel plate and to have lower cost.
V:V and C forms VC, and tiny VC can play certain inhibition to dislocation, improves the intensity of steel plate, but the more VC particle that can form alligatoring of V content, reduce the impact property of steel plate, in conjunction with other alloying element in the present invention, add the V of 0 ~ 0.07% to ensure the mechanical property of steel plate.
B: alloying element B can improve the hardening capacity of steel plate, makes steel plate more easily form the martensitic stucture of refinement when quench cooled, improves the mechanical property of steel plate.B too high levels, can cause more B in crystal boundary enrichment, reduces crystal boundary and combines energy, cause the low-temperature impact toughness of steel plate to reduce.Therefore, in the present invention, the add-on of B is 0.0006 ~ 0.0025%.
Al:Al forms tiny AlN and separates out when making steel, in process of cooling subsequently, suppress Austenite Grain Growth, reaches austenite crystal grain thinning, improves the object of steel toughness at low temperatures.Al too high levels can cause the oxide compound of larger Al to be formed, and steel-plate ultrasound wave inspection is not conformed to, and therefore adds the toughness of the Al raising steel plate of 0.01 ~ 0.08% in the present invention.
Ti：。C and N in Ti and steel forms compound, and the formation temperature of TiN is more than 1400 DEG C, usually separates out in liquid phase or delta ferrite, realizes the object of fining austenite grains.Ti too high levels, can form thick TiN and separate out, and cause the impact property of steel plate and fatigue property to reduce, the Ti content therefore in the present invention controls 0.003 ~ 0.06%.
H:H is subject to the effect in the edge dislocation hydrostaticpressure field of force in steel plate, can assemble, form hydrogen embrittlement at fault location.Intensity rank 1100MPa and with in upper steel plate, defect is more, as H content is too high, then after steel plate quenching and tempering heat treatment, the H atom that fault location enrichment is more, forms H molecule, cause steel plate generation delayed fracture, the H content therefore in the present invention controls be no more than 0.00018%.
N, O:N form AlN or TiN at steel grade, and play the effect of fining austenite grains, but N content increase and decrease can cause it in fault location enrichment, affects steel plate low-temperature impact work, therefore N content controls be no more than 0.0040%.The Al of O and steel grade forms Al
2o
3, TiO etc., be ensure steel plate homogeneity of structure and low-temperature impact work, O content is no more than 0.0030%.
The welding property of carbon equivalent and steel plate has substantial connection, usually adopts formula CEQ=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, calculates the carbon equivalent of steel plate.For ensureing the welding property of steel plate, steel plate carbon equivalent ce Q≤0.60% of the present invention.
Chemical composition of the present invention relates to the component system adopting and optimize, the alloys producing of Appropriate application, such as, when improving carbon content, adopts the alloying elements such as low Mn, Ni to ensure that carbon equivalent is not more than 0.60%.The optimal control of Cr, Mo and Ni element, to obtain the matched well of obdurability.The content of control P, S, N, O and H, ensures the low-temperature impact toughness of steel plate.Produce the yield strength 1100MPa grade high-strength steel plate with better welding property and obdurability coupling.
The manufacture method of yield strength 1100MPa grade super strength steel plate of the present invention, it comprises the steps:
4) smelt, cast,
Smelt by mentioned component, casting adopts die casting or continuous casting to become steel billet;
5) heating, rolling,
Heating temperature 1050 ~ 1250 DEG C, in the operation of rolling, steel billet starts rolling after going out process furnace, is rolled down to air cooling or slow cooling after appointed thickness;
6) quenching, tempering
The austenitizing temperature of quenching heat treatment is 850 ~ 950 DEG C, adopts Water Quenching after austenitizing; Tempering heat treatment temperature 160-350 DEG C, air cooling after tempering.
Steel plate of the present invention is at 1050 DEG C ~ 1250 DEG C heating austenitizings.In heat-processed, the carbonitride of Nb, V and Ti, the carbide portion of Cr and Mo or be all dissolved in austenite, in rolling subsequently and process of cooling, Nb, V and Ti form tiny carbonitride, anchoring austenite grain boundary, and refinement steel plate rolls state tissue.Cr and Mo is solid-solubilized in austenite, improves the hardening capacity of steel plate.Cr and Mo be solid-solubilized in austenite improves martensitic hardenability when quenching, and forms the tough microtexture of height with refinement martensite lath.
Quenching after steel plate rolling cooling post-heating to 850 ~ 950 DEG C of insulations.In heat-processed, the carbonitride of carbide forming element Nb, V, Ti, Cr and Mo is partly dissolved.Part undissolved carbonitride anchoring austenite grain boundary, avoids austenite crystal too thick, reduces the impelling strength of final steel plate.In quench cooled process, the alloying element be solid-solubilized in austenite improves the hardening capacity of steel plate, and make final martensite more tiny, this class loading has superstrength and good toughness.
Steel plate after quenching does tempering heat treatment at 160 ~ 350 DEG C.In quenching process, steel plate generation martensitic transformation, forms the martensitic stucture that defect concentration is larger, and there is larger strain strain energy steel plate inside, internal stress skewness.For improving the interior state of steel plate, and ensure good mechanical property, need in suitable temperature tempering.In tempering range of the present invention, the internal stress of steel plate can be reduced, be conducive to the follow-up machine-shaping of steel plate, can ensure that steel plate has good obdurability simultaneously.
The present invention is compared with prior art:
The High Strength Steel Plate of patent publication No. WO 1999005335, adopts the low-carbon (LC) height Mn component system of C:0.05-0.10% and Mn:1.7-2.1% and cooling controlling and rolling controlling process to obtain tensile strength and is greater than 930MPa steel plate.
Chinese patent CN101497971 " a kind of high-strength hardened and tempered steel and production method thereof ", adopt C:0.07-0.11%, Mn:1.48-1.60%, the microalloy component system of Ni:0.18-0.40%, adopt the operational path of two-phase control rolling, ACC, quenching+tempering, develop yield strength >=670MPa, the high tensile steel plate of tensile strength >=770MPa.
The alloying element content of above two patents is different from the present invention, and the strength property that product of the present invention reaches is better than above-mentioned patent.
Chinese patent CN1840723A discloses " superhigh strength steel plate with yield strength more than 1100 Mpa and manufacture method thereof ", this patent have employed the design of alloy of low Al, and define the comparatively high Mn content upper limit, containing alloying element Ca, during the design of other alloying element, do not consider its impact on carbon equivalent.The present invention adopts higher Al content crystal grain thinning, not containing alloying element Ca, define the content of the interstitial atom elements such as N, O, H, and by suitable composition proportion, carbon equivalent C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15≤0.60% can be met, there is better welding property.
Chinese patent CN1840723A adopts press quenching+tempering process, and the present invention adopts the operational path of quenching+tempering, can produce the steel plate with better microstructure and mechanical property homogeneity, and therefore the present invention is all better than above-mentioned patent from Composition Design and technological design.
Yield strength >=1100MPa of the present invention, tensile strength >=1250MPa, all far above foregoing invention patent, and carbon equivalent≤0.60%, have good welding property, and the present invention adopts quenching to add the thermal treatment process of tempering, composition and technique are all creative.
Beneficial effect of the present invention
1, by rational designing chemical composition and combined process, develop yield strength 1100MPa grade super strength steel plate, this steel has excellent toughness at low temperatures.Adopt low-temperaturetempering technique after steel plate quenching, eliminate the internal stress of steel plate and ensure the low temperature impact properties of steel plate.
2, the composition of steel plate and technological design reasonable, process window is loose, can produce line realizes batch commercially produce at plate of moderate thickness.
3, steel plate yield strength >=1100MPa, tensile strength >=1250MPa, Xia Shi Impact energy Ak v(-40 DEG C of the present invention's production) >=50J, carbon equivalent≤0.60%.Steel plate has superstrength and obdurability coupling, and carbon equivalent is lower, has good welding property.
Accompanying drawing explanation
Fig. 1 is microstructure morphology (500 ×) photo of the embodiment of the present invention 3 steel plate.
Fig. 2 is microstructure morphology (200 ×) photo of the embodiment of the present invention 3 steel plate.
Embodiment
For a more detailed description to the present invention by reference to the accompanying drawings by embodiment below.These embodiments are only the descriptions to best mode for carrying out the invention, do not have any restriction to scope of the present invention.
The composition of steel plate embodiment of the present invention is in table 1.
In heat-processed, Heating temperature is 1050 ~ 1250 DEG C.During the operation of rolling, steel plate starts rolling after coming out of the stove.In process of cooling, steel plate air cooling or slow cooling.In quenching process, austenitizing temperature is 850 ~ 950 DEG C.Tempering temperature is 160 ~ 350 DEG C.
Embodiment 1
By the chemical composition electric furnace shown in table 2 or converter smelting, and be cast into continuously cast bloom or steel ingot, by continuously cast bloom or Heating Steel Ingots to 1050 DEG C, start rolling temperature is 1020 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 860 DEG C, and finished steel plate thickness is 8mm.Air cooling after rolling.Quenching temperature is 850 DEG C.Tempering temperature is 350 DEG C.
Embodiment 2
Embodiment is with embodiment 1, and wherein Heating temperature is 1080 DEG C, and start rolling temperature is 1060 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 870 DEG C, and finished steel plate thickness is 10mm.Air cooling after rolling.Quenching temperature is 880 DEG C.Tempering temperature is 320 DEG C.
Embodiment 3
Embodiment is with embodiment 1, and wherein Heating temperature is 1110 DEG C, and start rolling temperature is 1100 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 930 DEG C, and finished steel plate thickness is 12mm.Air cooling after rolling.Quenching temperature is 900 DEG C.Tempering temperature is 280 DEG C.
Embodiment 4
Embodiment is with embodiment 1, and wherein Heating temperature is 1150 DEG C, and start rolling temperature is 1100 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 1050 DEG C, and finished steel plate thickness is 15mm.Air cooling after rolling.Quenching temperature is 910 DEG C.Tempering temperature is 240 DEG C.
Embodiment 5
Embodiment is with embodiment 1, and wherein Heating temperature is 1180 DEG C, and start rolling temperature is 1110 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 990 DEG C, and finished steel plate thickness is 20mm.Air cooling after rolling.Quenching temperature is 920 DEG C.Tempering temperature is 200 DEG C.
Embodiment 6
Embodiment is with embodiment 1, and wherein Heating temperature is 1250 DEG C, and start rolling temperature is 1200 DEG C, and pass deformation rate is 5 ~ 30%, and finishing temperature is 1010 DEG C, and finished steel plate thickness is 30mm.Slow cooling after rolling.Quenching temperature is 950 DEG C.Tempering temperature is 160 DEG C.
Table 1 embodiment chemical composition (wt.%)
Carry out Mechanics Performance Testing to the yield strength 1100MPa level high strength steel plate of embodiment of the present invention 1-6, test result is in table 2.
The mechanical property of the steel plate of table 2 embodiment of the present invention 1-6
As can be seen from table 2, table 3, the yield strength of the yield strength 1100MPa level hypervelocity steel plate that the present invention relates to all >=1100MPa, tensile strength >=1250MPa, Xia Shi Impact energy Ak v(-40 DEG C) >=50J.
See Fig. 1, Fig. 2, embodiment 3 is carried out to the optical microscope photograph of microtexture research, as can be seen from Fig. 1, Fig. 2, the microtexture of steel plate is the tempered martensite of refinement.
Claims (2)
1. a yield strength 1100MPa grade high-strength steel plate, its chemical component weight per-cent is:
C:0.15～0.25%
Si:0.10～0.50%
Mn:0.60～1.20%
P:≤0.013%
S:≤0.003%
Cr:0.20～0.55%
Mo:0.20～0.70%
Ni:0.60～2.00%
Nb:0～0.07%
V:0～0.07%
B:0.0006～0.0025%
A1:0.01～0.08%
Ti:0.003～0.06%
H:≤0.00018%
N≤0.0040%
O≤0.0030%
All the other are Fe and inevitable impurity; And, carbon equivalent ce Q≤0.60%; Obtain tempered martensite, the yield strength >=1100MPa of steel plate, tensile strength >=1250MPa, Xia Shi Impact energy Ak v(-40 DEG C) >=50J; It adopts following manufacture method:
1) smelt, cast,
Smelt by mentioned component, casting adopts die casting or continuous casting to become steel billet;
2) heating, rolling,
Heating temperature 1050 ~ 1250 DEG C, in the operation of rolling, steel billet starts rolling after going out process furnace, is rolled down to air cooling or slow cooling after appointed thickness;
3) quenching, tempering
The austenitizing temperature of quenching heat treatment is 850 ~ 950 DEG C, adopts Water Quenching after austenitizing; Tempering heat treatment temperature 160 ~ 350 DEG C, air cooling after tempering.
2. a manufacture method for yield strength 1100MPa grade super strength steel plate, it comprises the steps:
1) smelt, cast,
2) smelt by following compositions, casting adopts die casting or continuous casting to become steel billet; Its chemical component weight per-cent is: C:0.15 ~ 0.25%, Si:0.10 ~ 0.50%, Mn:0.60 ~ 1.20%, P :≤0.013%, S :≤0.003%, Cr:0.20 ~ 0.55%, Mo:0.20 ~ 0.70%, Ni:0.60 ~ 2.00%, Nb:0 ~ 0.07%, V:0 ~ 0.07%, B:0.0006 ~ 0.0025%, Al:0.01 ~ 0.08%, Ti:0.003 ~ 0.06%, H :≤0.00018%, N≤O.0040%, O≤0.0030%, all the other are Fe and inevitable impurity, and, carbon equivalent ce Q≤0.60%; Heating, rolling,
Heating temperature 1050 ~ 1250 DEG C, in the operation of rolling, steel billet starts rolling after going out process furnace, is rolled down to air cooling or slow cooling after appointed thickness;
3) quenching, tempering
The austenitizing temperature of quenching heat treatment is 850 ~ 950 DEG C, adopts shrend place after austenitizing
Reason; Tempering heat treatment temperature 160 ~ 350 DEG C, air cooling after tempering;
Obtain tempered martensite, the yield strength >=1100MPa of steel plate, tensile strength >=1250MPa, Xia Shi Impact energy Ak v(-40 DEG C) >=50J.
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