CN102747303A - 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 have the ultrahigh-strength steel plates of good low-temperature toughness, be specifically related to ys 1100MPa grade high-strength steel plate and method of manufacture thereof.
Background technology
High tensile steel plate is used and equipments such as coal mine machinery such as coal mine hydraulic supporting etc., engineering machinery such as crawler mounted crane, crane and truck etc. and large-scale floating crane peculiar to vessel.Physical construction is on active service in big load and complex environment usually, so physical construction requires steel plate that higher intensity and good low-temperature flexibility are arranged with high tensile steel plate.The high tensile steel plate that present Europe superscript EN10025 and GB 16270 relate to, its ys is up to 960MPa.Ultra-large type engineering machinery such as large-tonnage crawler mounted crane and crane etc. all need use ys 1100MPa grade steel plate at present.
Choose suitable chemical ingredients,, can produce the high tensile steel plate that satisfies the machinofacture customer need in conjunction with controlled rolling controlled chilling or the Q-tempering technology optimized.Adopt the controlled rolling and controlled cooling mode to produce high tensile steel plate, the control difficulty is bigger in rolling and process of cooling, influences the whole homogeneity of steel plate mechanical property.Adopt Q-tempering explained hereafter high tensile steel plate, the hardening capacity of the content raising steel plate through alloying element and carbon makes steel plate in process of cooling, form martensitic stucture.Martensite is that carbon is solid-solubilized in the iron atom body centered structure, the tetragonal lattice that the bcc lattice is extended to form along the c direction of principal axis, and this type of tissue has higher intensity and hardness.Martensite forms with side cut phase transformation mode, and the forward position of phase transformation is a row glissile dislocation, and side cut can cause the surface relief effect, is cut edge by crystal and causes martensitic stucture strain energy storage bigger, reaches 1000J/mol even higher.The martensitic stucture that side cut forms is tiny, and defect concentration is bigger between the martensite lamella.Bigger defect concentration is that tiny crack shape is closed the source of growing up, and under stressed effect, can form tiny crack, and tiny crack is grown up and made steel plate and rupture rapidly along crystal boundary, and the low-temperature impact work of high tensile steel plate that therefore has martensitic stucture is lower.Therefore, need through optimized composition and technology, 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 ys 1100MPa grade super strength steel plate and method of manufacture thereof, adopt quenching-and-tempering process, ys 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 ys 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 unavoidable impurities,
And, carbon equivalent ce Q≤0.60%; Obtain tempered martensite, the ys>=1100MPa of steel plate, tensile strength>=1250MPa, Xia Shi ballistic work Akv (40 ℃)>=50J.
In composition design of the present invention:
C:C doses in the steel, improves the hardening capacity of steel plate, makes steel plate in the quench cooled process, form the higher martensitic stucture of hardness.C content improves, and then martensite hardness increases, and correspondingly the intensity of steel plate increases, but can cause toughness to descend.C content increases, and can cause the welding property variation of steel plate, comprehensive obdurability and welding property, and in the patent of the present invention, setting carbon content is 0.15 ~ 0.25%.
Si:Si substitutes the Fe atom with substitute mode in steel, hinder dislocation motion, improves the strength property of steel plate.Therefore Si can reduce C diffusibility in ferritic, and an amount of Si can avoid forming thick carbide and separates out at fault location when tempering.The higher welding property that can worsen steel plate of Si content.Therefore the Si content among steel plate the present invention is controlled to be Si:0.10 ~ 0.50%.
Mn:Mn is weak carbide forming element, and the Mn in the steel mainly exists with the solid solution form.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 type of tissue has good obdurability coupling.The higher meeting of Mn content causes that the Mn segregation is arranged in the steel plate, worsens the steel plate interior tissue, possibly form bigger MnS simultaneously and be mingled with, and causes UT not conform to.Add 0.60 ~ 1.20% Mn among the present invention, help improving the hardening capacity of steel plate, and reduce the influence of center segregation steel plate.
P: P gathers at crystal boundary partially in the steel, can reduce the bound energy of crystal boundary, reduces the low temperature impact properties of steel plate.There are the temper brittleness that can aggravate steel jointly in P and Mn.The P that gathers partially at crystal boundary can make steel plate take place to form bigger cleavage surface along brilliant fracture in the time spent of doing that receives shock load, reduces steel plate and is receiving the energy that absorbs when impacting.P can worsen the welding property of steel, and therefore for welding, the P content that need try one's best low guarantees weldableness.Adding is no more than 0.013% P among the present invention, guarantees 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 the solidification of molten steel process, S can take place to gather partially, forms more sulfide inclusion, the UT performance and the low temperature impact properties of harm steel plate.In the welding process, S causes thermal crack easily, because S is prone to oxidation, generates SO simultaneously
2Gas evolution produces pore with loose in welding base metal.Adding is no more than 0.003% S among the present invention, guarantees that steel plate has good low temperature impact properties and obdurability coupling.
Cr:Cr doses in the steel, can suppress the diffusion transformation of steel plate, improves the hardening capacity of steel plate, forms the hardened martensitic stucture, obtains to have the steel plate of higher-strength.The Cr too high levels can cause the welding property of steel plate to reduce, so adds 0.20 ~ 0.55% Cr among the present invention, guarantees the intensity and the welding property of steel plate.
Mo:Mo can improve the hardening capacity of steel plate, makes steel plate in quenching process, form martensite.If quenching velocity is very fast, and in the lower temperature range tempering, then Mo mainly is present in the steel with the solid solution form, plays solid solution strengthening effect.Dose the Mo of certain content in the steel; Can improve the intensity of steel plate, and can not worsen the low temperature impact properties of steel plate, but higher Mo can worsen the steel plate welding property; Therefore the Mo that adds 0.20-0.70% in the patent of the present invention is to obtain the coupling of obdurability and welding property.
Nb:Nb adds in the steel, plays the restraining effect to steel plate recrystallization, makes steel plate at the lesser temps recrystallize, refine austenite, thus reach the final purpose of organizing of refinement.Nb content is higher, can form thicker NbC particle at the crystal boundary place, causes the low temperature impact properties of steel plate to worsen.Cooperate other alloying element, add 0 ~ 0.07% Nb among the present invention to guarantee the mechanical property of steel plate.
Ni:Ni exists with the solid solution form in steel, and in composition system of the present invention, Ni exists with the FCC of Fe-Ni-Mn mutually, reduces stacking fault energy, improves the low temperature impact properties of steel plate.Ni belongs to noble metal, and higher Ni content can cause the steel plate production cost to increase, thus add among the present invention 0.60 ~ 2.00% Ni with the mechanical property that guarantees steel plate with have lower cost.
V:V and C form VC, and tiny VC can play certain inhibition to dislocation, improve the intensity of steel plate; But the more VC particle that can form alligatoring of V content; Reduce the impact property of steel plate, combine other alloying element among the present invention, the V of adding 0 ~ 0.07% is to guarantee the mechanical property of steel plate.
B: alloying element B can improve the hardening capacity of steel plate, makes steel plate when quench cooled, form the martensitic stucture of refinement more easily, improves the mechanical property of steel plate.The B too high levels can cause more B in the crystal boundary enrichment, reduces the crystal boundary bound energy, causes the low-temperature impact toughness of steel plate to reduce.Therefore, the add-on of B is 0.0006 ~ 0.0025% among the present invention.
Al:Al forms tiny AlN and separates out when steel-making, in process of cooling subsequently, suppress austenite crystal and grow up, and reaches the austenite crystal grain thinning, improves steel flexible purpose at low temperatures.The Al too high levels can cause the oxide compound of bigger Al to form, and the steel-plate ultrasound wave inspection is not conformed to, so adds the toughness that 0.01 ~ 0.08% Al improves steel plate among the present invention.
Ti：。C in Ti and the steel and N form compound, and the formation temperature of TiN is more than 1400 ℃, in liquid phase or delta ferrite, separate out usually, realize the purpose of refine austenite crystal grain.The Ti too high levels can form thick TiN and separate out, and cause the impact property of steel plate and fatigue property to reduce, so the Ti content among the present invention is controlled at 0.003 ~ 0.06%.
H:H receives the effect in the edge dislocation hydrostaticpressure field of force in the steel plate, can assemble at fault location, forms hydrogen embrittlement.Intensity rank 1100MPa reaches with in the upper steel plate, and defective is more, like the H too high levels; Then after steel plate quenching and tempering heat treatment, the H atom that the fault location enrichment is more forms the H molecule; Cause steel plate generation delayed fracture, so the H content among the present invention is controlled at and is no more than 0.00018%.
N, O:N forms AlN or TiN at steel grade, play the effect of refine austenite crystal grain, but the increase and decrease of N content can cause it in the fault location enrichment, influences the steel plate low-temperature impact work, so N content is controlled at and is no more than 0.0040%.The Al of O and steel grade forms Al
2O
3, TiO etc., be to guarantee 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, adopts formula CEQ=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15 usually, calculates the carbon equivalent of steel plate.For guaranteeing the welding property of steel plate, steel plate carbon equivalent ce Q of the present invention≤0.60%.
Chemical ingredients of the present invention relates to the composition system of optimizing that adopts, and the effect of the alloying element that rationally utilizes for example when improving carbon content, adopts alloying elements such as low Mn, Ni to be not more than 0.60% to guarantee carbon equivalent.Cr, Mo and the optimal control of Ni element are to obtain the matched well of obdurability.The content of control P, S, N, O and H, the low-temperature impact toughness of assurance steel plate.Production has the ys 1100MPa grade high-strength steel plate of better welding property and obdurability coupling.
The method of manufacture of ys 1100MPa grade super strength steel plate of the present invention, it comprises the steps:
4) smelt, cast,
Press mentioned component and smelt, casting adopts die casting or continuous casting to become steel billet;
5) heating, rolling,
1050 ~ 1250 ℃ of Heating temperatures, in the operation of rolling, it is rolling that steel billet goes out behind the process furnace beginning, is rolled down to air cooling or slow cooling after the appointed thickness;
6) quenching, tempering
The austenitizing temperature of quenching heat treatment is 850 ~ 950 ℃, adopts Water Quenching behind the austenitizing; 160-350 ℃ of tempering heat treatment temperature, air cooling after the tempering.
Steel plate of the present invention is at 1050 ℃～1250 ℃ heating austenitizings.In the heat-processed, the carbide portion of the carbonitride of Nb, V and Ti, Cr and Mo or all be dissolved in the austenite, in rolling and process of cooling subsequently, Nb, V and Ti form tiny carbonitride, the anchoring austenite grain boundary, the refinement steel plate rolls the attitude tissue.Cr and Mo are solid-solubilized in the austenite, improve the hardening capacity of steel plate.The Cr and the Mo that are solid-solubilized in the austenite improve martensitic hardenability when quenching, form to have the high tough microtexture of refinement martensite lath.
Quench after steel plate rolling cooling post-heating to the 850 ~ 950 ℃ insulation.In the heat-processed, the carbonitride of carbide forming element Nb, V, Ti, Cr and Mo is partly dissolved.The undissolved carbonitride anchoring of part austenite grain boundary avoids austenite crystal too thick, reduces the impelling strength of final steel plate.In the quench cooled process, be solid-solubilized in the hardening capacity of the alloying element raising steel plate in the austenite, make that final martensite is more tiny, this type of tissue has superstrength and good toughness.
Steel plate after the quenching is done tempering heat treatment at 160 ~ 350 ℃.In the quenching process, steel plate generation martensitic transformation forms the bigger martensitic stucture of defect concentration, and there are bigger strain strain energy, internal stress skewness in steel plate inside.For improving the interior state of steel plate, and guarantee mechanical property preferably, need in suitable temperature tempering.In tempering range according to the invention, can reduce the internal stress of steel plate, help the follow-up machine-shaping of steel plate, can guarantee 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 low-carbon (LC) high Mn composition system and the cooling controlling and rolling controlling process of C:0.05-0.10% and Mn:1.7-2.1% to obtain tensile strength greater than the 930MPa steel plate.
Chinese patent CN101497971 " a kind of high-strength hardened and tempered steel and working method thereof "; Adopt C:0.07-0.11%; Mn:1.48-1.60%, the microalloy composition system of Ni:0.18-0.40% adopts two stage rolling, ACC, quenching+tempered operational path; Developed ys >=670MPa, the high tensile steel plate of tensile strength >=770MPa.
More than the alloying element content of two patents different with the present invention, and the strength property that product according to the invention reaches is superior to above-mentioned patent.
Chinese patent CN1840723A discloses " above ultrahigh-strength steel plates of ys 1100MPa and method of manufacture thereof "; This patent has adopted the design of alloy of low Al; And stipulated higher Mn upper content limit; Contain alloying element Ca, do not consider its influence during other alloying element design carbon equivalent.The present invention adopts higher Al content crystal grain thinning; Do not contain alloying element Ca, stipulated the content of interstitial atom elements such as N, O, H, and through the appropriate ingredients proportioning; Can satisfy carbon equivalent C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15≤0.60%, have better welding property.
Chinese patent CN1840723A adopts press quenching+tempering process, and the present invention adopts quenching+tempered operational path, can produce to have better tissue and the inhomogeneity steel plate of mechanical property, so the present invention all is superior to above-mentioned patent from the design of composition design and processes.
Ys>=1100MPa of the present invention, tensile strength>=1250MPa all far above the foregoing invention patent, and carbon equivalent≤0.60%, has good welding property, and the present invention adopts to quench and add the tempered thermal treatment process, and composition and technology are all creative.
Beneficial effect of the present invention
1, through rational designing chemical composition and combined process, develop ys 1100MPa grade super strength steel plate, this steel has excellent toughness at low temperatures.Adopt low-temperaturetempering technology behind the steel plate quenching, eliminated the internal stress of steel plate and guaranteed the low temperature impact properties of steel plate.
2, the composition of steel plate and technological design are reasonable, and process window is loose, can produce at plate and realize on the line commercially producing in batches.
3, steel plate ys>=1100MPa, tensile strength>=1250MPa, the Xia Shi ballistic work Akv (40 ℃)>=50J of the present invention's production, carbon equivalent≤0.60%.Steel plate has superstrength and obdurability coupling, and carbon equivalent is lower, has good welding property.
Description of drawings
Fig. 1 is microtexture pattern (500 *) photo of the embodiment of the invention 3 steel plates.
Fig. 2 is microtexture pattern (200 *) photo of the embodiment of the invention 3 steel plates.
Embodiment
Below combine accompanying drawing that the present invention is made more detailed description with embodiment.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
The composition of steel plate embodiment of the present invention is seen table 1.
In heat-processed, Heating temperature is 1050 ~ 1250 ℃.During the operation of rolling, begin rolling after steel plate is come out of the stove.In the process of cooling, steel plate air cooling or slow cooling.Austenitizing temperature is 850 ~ 950 ℃ in the quenching process.Tempering temperature is 160 ~ 350 ℃.
Embodiment 1
Press chemical ingredients electric furnace or the converter smelting shown in the table 2, and be cast into continuously cast bloom or steel ingot, continuously cast bloom or steel ingot are heated to 1050 ℃, start rolling temperature is 1020 ℃, and pass deformation rate is 5～30%, and finishing temperature is 860 ℃, and the Finished Steel plate thickness is 8mm.Rolling back air cooling.Quenching temperature is 850 ℃.Tempering temperature is 350 ℃.
Embodiment 2
Embodiment is with embodiment 1, and wherein Heating temperature is 1080 ℃, and start rolling temperature is 1060 ℃, and pass deformation rate is 5～30%, and finishing temperature is 870 ℃, and the Finished Steel plate thickness is 10mm.Rolling back air cooling.Quenching temperature is 880 ℃.Tempering temperature is 320 ℃.
Embodiment 3
Embodiment is with embodiment 1, and wherein Heating temperature is 1110 ℃, and start rolling temperature is 1100 ℃, and pass deformation rate is 5～30%, and finishing temperature is 930 ℃, and the Finished Steel plate thickness is 12mm.Rolling back air cooling.Quenching temperature is 900 ℃.Tempering temperature is 280 ℃.
Embodiment 4
Embodiment is with embodiment 1, and wherein Heating temperature is 1150 ℃, and start rolling temperature is 1100 ℃, and pass deformation rate is 5～30%, and finishing temperature is 1050 ℃, and the Finished Steel plate thickness is 15mm.Rolling back air cooling.Quenching temperature is 910 ℃.Tempering temperature is 240 ℃.
Embodiment 5
Embodiment is with embodiment 1, and wherein Heating temperature is 1180 ℃, and start rolling temperature is 1110 ℃, and pass deformation rate is 5～30%, and finishing temperature is 990 ℃, and the Finished Steel plate thickness is 20mm.Rolling back air cooling.Quenching temperature is 920 ℃.Tempering temperature is 200 ℃.
Embodiment 6
Embodiment is with embodiment 1, and wherein Heating temperature is 1250 ℃, and start rolling temperature is 1200 ℃, and pass deformation rate is 5～30%, and finishing temperature is 1010 ℃, and the Finished Steel plate thickness is 30mm.Rolling back slow cooling.Quenching temperature is 950 ℃.Tempering temperature is 160 ℃.
Table 1 embodiment chemical ingredients (wt.%)
Ys 1100MPa level high strength steel plate to embodiment of the invention 1-6 carries out Mechanics Performance Testing, and test result is seen table 2.
The mechanical property of the steel plate of table 2 embodiment of the invention 1-6
Can find out from table 2, table 3, the ys of the ys 1100MPa level hypervelocity steel plate that the present invention relates to all >=1100MPa, tensile strength >=1250MPa, Xia Shi ballistic work Akv (40 ℃) >=50J.
Referring to Fig. 1, Fig. 2,, can find out from Fig. 1, Fig. 2 that the microtexture of steel plate is the tempered martensite of refinement to the optical microscope photograph that embodiment 3 carries out microtexture research.
Claims (2)
1. ys 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 unavoidable impurities,
And, carbon equivalent ce Q≤0.60%; Obtain tempered martensite, the ys>=1100MPa of steel plate, tensile strength>=1250MPa, Xia Shi ballistic work Akv (40 ℃)>=50J.
2. the method for manufacture of ys 1100MPa grade super strength steel plate as claimed in claim 1, it comprises the steps:
1) smelt, cast,
Press mentioned component and smelt, casting adopts die casting or continuous casting to become steel billet;
2) heating, rolling,
1050 ~ 1250 ℃ of Heating temperatures, in the operation of rolling, it is rolling that steel billet goes out behind the process furnace beginning, is rolled down to air cooling or slow cooling after the appointed thickness;
3) quenching, tempering
The austenitizing temperature of quenching heat treatment is 850 ~ 950 ℃, adopts Water Quenching behind the austenitizing; 160 ~ 350 ℃ of tempering heat treatment temperature, air cooling after the tempering.
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