CN101660104A - High-temperature resistant tempered heavy plate with low susceptibility to welding crack and production method thereof - Google Patents
High-temperature resistant tempered heavy plate with low susceptibility to welding crack and production method thereof Download PDFInfo
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Abstract
The invention discloses a high-temperature resistant tempered heavy plate with low susceptibility to welding crack and a production method thereof. The heavy plate comprises the following chemical compositions in percentage by weight: 0.08 to 0.11 percent of C, 0.15 to 0.40 percent of Si, 1.20 to 1.75 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.006 percent of S, 0.20 to 0.45 percent of Ni, 0.15 to 0.30 percent of Cr, 0.20 to 0.40 percent of Mo, 0.10 to 0.30 percent of Cu, 0.03 to 0.06 percent of V, 0.04 to 0.06 percent of Nb, 0.025 to 0.035 percent of Als,0.015 to 0.025 percent of Ti and the balance of iron and inevitable impurities; and the chemical compositions meet a condition that: P cm is equal to C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B and is less than or equal to 0.26 percent. A production process for controlling a rolling process in two stages of an austenite complete recrystallization region and an austenite non-recrystallization region,forcedly cooling on line and tempering is adopted, a parent metal steel plate is tempered at 680DEG C, can still maintain the stability of textures and performance, and has the tensile strength above780MPa.
Description
Technical field
The present invention relates to tensile strength 〉=780MPa level high-temperature resistant tempered heavy plate with low susceptibility to welding crack and production method thereof, belong to low alloy steel and make the field.
Background technology
Before the present invention, " 780MPa level high-tensile steel and manufacture method thereof " (patent No. JP2007063603) discloses tensile strength 780MPa level low-welding crack-sensitive quenched and tempered steel and production technology thereof.Its objective is the steel plate and the production method thereof that the 780MPa level are provided, have excellent in toughness and anti-reheat crack(ing) characteristic.Chemical ingredients contains B.
Before the present invention, in " non-modified Plate Steel of 780MPa level and manufacture method " (patent No. JP2004052063) document tensile strength 780MPa level low-welding crack-sensitive non-hardened and tempered steel and production technology thereof are disclosed.Its objective is provides the 780MPa level, has non-modified slab of good low-temperature flexibility and production method thereof.Chemical ingredients contains B.
So far, tensile strength 780MPa level low welding crack sensibility high-strength steel slab adopts modified and the non-tempering process production technology basically, nearly all is by adding the hardening capacity that B guarantees steel.With B guarantee steel intensity, increase the hardening capacity of steel, chemical ingredients and create conditions and will influence each other may cause the hardness of mother metal unstable properties, particularly welded heat affecting zone to significantly improve.
" production with good welds and low-temperature flexibility steel plate " (patent No. JP8013032) introduced the production method of 780MPa rank low welding crack sensibility high-strength steel slab, adopts isothermal quenching technique.
" 780MPa level high-tensile steel and manufacture method thereof " (patent No. JP2007063603) document provides the 780MPa level else to have the production method of good welds crack sensitive steel.But Mo, V, Ti content in the steel are limited with formula Mo+2.9V+2Ti≤0.50%.
Summary of the invention
The object of the present invention is to provide a kind of high-temperature resistant tempered heavy plate with low susceptibility to welding crack and production method thereof, steel plate tensile strength 〉=780MPa, the steel plate maximum ga(u)ge reaches 40mm.The excellent properties that steel plate has low-welding crack-sensitive and has high tempering stability.The chemical ingredients of design is simple and production technique is easy, is fit to produce in batches.
The present invention has designed a kind of high-temperature resistant tempered steel of low-welding crack-sensitive that has to achieve the above object, it is characterized in that the weight percent of the chemical ingredients of steel is:
C?0.08％～0.11％、Si?0.15％～0.40％、Mn?1.20％～1.75％、P≤0.020％、S≤0.006％、Ni?0.20％～0.45％、Cr?0.15％～0.30％、Mo?0.20％～0.40％、Cu?0.10％～0.30％、V0.03％～0.06％、Nb?0.04％～0.06％，Als?0.025％～0.035％，Ti?0.015％～0.025％。Surplus is Fe and unavoidable impurities.In addition, steel chemical composition of the present invention also must satisfy:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.26％；
Details are as follows for the reason of interalloy Elements C of the present invention, Si, Mn, P, S, Al, Ni, Cr, Mo, Cu, V, Nb, Ti limited amount:
C:C≤0.06% o'clock need add other and improve the hardening capacity element, and cost is raise, and toughness and weldability degenerate.Particularly under the situation of big welding energy of the present invention, C≤0.06% o'clock, C to the diffusion of molten metal seldom is difficult to guarantee strength of welded joint with general welding material.Macro-energy welding joint toughness for after guaranteeing welding crack sensibility and adding Nb is limited to 0.11% on the C.The design of this steel grade C composition is limited to 0.08% consideration proof strength down and designs.
Si: play a role in guaranteeing strength of parent and strength of welded joint for making Si, Si should be greater than 0.15%, but Si＞0.40% o'clock, welding crack sensibility and welding joint toughness degenerate.Its content is controlled at: 0.15%～0.40%.
Mn: guaranteeing that for making Mn strength of parent and strength of welded joint play a role, its content answers 〉=1.20%.But Mn＞1.75% o'clock degenerates welding crack sensibility, and brings excessive hardening capacity that base metal tenacity and joint toughness are degenerated because content is too high.Its content is controlled at: 1.20%～1.75%.
P, S:P, S are impurity element in this steel grade.Be limited in P≤0.020%; S≤0.006%.
It is to reduce the amount and the size thereof of M-A constituent element that Al:Al improves coarse grain zone flexible mechanism, has reduced solid solution N amount.The solvent temperature of AlN is near 1100 ℃, and it is easy to dissolving in Thermal Cycle, can not stop the grain growth of HAZ effectively.The AlN particle can dissolve in Thermal Cycle, makes that the content of free N increases among the HAZ.Separating out of AlN is very slow, and AlN is difficult in the welding process again forming core and separates out.The content of Al is 〉=0.025% generally speaking, is limited to 0.035% on the adding Al.
Ti: according to the N content in the steel, suitably add Ti, it is best with the effect that alleviates the embrittlement of large-line energy welded heat affecting zone to form the particle that the disperse of TiN fine-grannular distributes, and austenitic crystal grain is thick when utilizing the throw out of TiN to suppress to weld, and increases the precipitation nuclear of acicular ferrite.3.42 be the desirable stoicheiometry of Ti in the steel, N atom.When the Ti/N value in the steel approaches desirable stoicheiometry, the more tiny and distribution disperse of TiN particle, the strongest to the refining effect of high temperature austenite crystal grain, the Ti/N value is excessive or too smallly all will slacken this effect.The content of Ti is: 0.015%～0.025%.
Nb:Nb combines with cooling controlling and rolling controlling process by microalloying and makes the abundant refinement of mother metal crystal grain, and in conjunction with precipitation strength and dislocation substructure strengthening effect, reaches the purpose that improves the mother metal over-all properties.Its content is controlled at: 0.04%～0.06%.
Ni, Cr:Ni, Cr help improving the intensity of mother metal and welding joint.Ni can further improve toughness.But surpass required amount Ceq is increased, cause the toughness reduction and the processibility of large-line energy welding joint to degenerate, so the content of Ni be: 0.20%～0.45% as addition; Cr 0.15%～0.30%.
Mo:Mo is effective to improving strength of parent and strength of welded joint, and Mo 0.20%～0.40%.
Cu:Cu is effective to improving strength of parent, and Cu 0.10%～0.30%.
V:V adds for guaranteeing strength of parent and strength of welded joint, and addition is 0.03%～0.06%.
The production method of high-temperature resistant tempered heavy plate with low susceptibility to welding crack of the present invention, Clean Steel technologies such as molten steel employing vacuum-treat are smelted, and online controlled rolling and controlled cooling and off-line tempering process are adopted in steel plate production.
Heating temperature before the hot rolling: Heating temperature is if surpass 1250 ℃, may cause steel original austenite grains thickization and can not guarantee the toughness of mother metal, so on be limited to 1250 ℃.The steel billet tapping temperature is 1150～1240 ℃.But consider the suitable dissolving of microalloy element, Heating temperature must guarantee 1150～1240 ℃.
Rolling condition:
Steel heating of the present invention back rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology.
The austenite recrystallization district is rolling: the fs of controlled rolling, temperature range is at 1150～1000 ℃.For guaranteeing base metal tenacity and avoiding producing the thick crystal grain of local anomaly, should make the single pass draft greater than 10%, should guarantee cumulative deformation 〉=55% in this stage.
Austenite non-recrystallization district is rolling: the subordinate phase of controlled rolling, temperature range be controlled at≤and 940 ℃.For thereby the effect that guarantees grain refining reaches yield strength and the flexible purpose that improves steel, should make the single pass draft, should guarantee cumulative deformation 〉=55% in this stage greater than 10%.
Online acceleration cooling:
After hot rolling finishes, the steel plate of temperature more than Ar3 forced cooling.When forcing cooling water is applied on the steel plate equably.The water temp of going into of steel plate is 840～860 ℃, and the final cooling temperature of steel plate is controlled at 280～350 ℃.The speed of cooling of steel plate is controlled at 25～35 ℃/S.The speed of cooling that should make thickness of slab 1/2 place 10 ℃/more than the S.
Temper:
The purpose of temper is implemented for eliminating stress.Also have in the present invention and make Nb and V carbide separate out the special role that improves and guarantee strength of parent.Can achieve the above object carrying out tempering more than 600 ℃.When 680 ℃ of tempering, metallographic structure not alligatoring and intensity keeps moderate.
Steel grade of the present invention adopts the low welding crack sensitivity steel composition design that does not contain B.Steel grade of the present invention can obviously suppress the forming core of ferrite on austenite grain boundary as the B that adds trace, and it is flat also to make the bainite transformation curve become ground simultaneously, thereby also can obtain bainite structure in a bigger cooling rate scope, makes steel grade improve intensity.But, because improving the effect of steel grade intensity, B is based on it in gathering and axle such as prevention ferrite preferential forming core on crystal boundary partially on the austenite grain boundary, must control B content during smelting, and operation brings great difficulty to smelting technology; If B is present in the steel with oxide compound or nitride, just lost the effect that suppresses ferrite forming core on crystal boundary, also control brings difficulty to smelting technology.In addition, in low-carbon bainite steel,, easily form the localized voids free zone and promote the intracrystalline crackle, cause the fluctuation of finished product steel plate toughness because the control of rolling and process for cooling is improper.So this steel grade has taked not contain the composition design of B.
Select for use not contain the design of B low alloy steel composition, adopt the TMCP explained hereafter steel grade of the present invention that limits cooling rate, obtain the 780MPa level low-welding crack-sensitive slab of high-temperature resistant tempered excellent property.This production method does not have unconventional technology difficulty, can reach than the more economical actual effect of off-line hardened and tempered steel plate production technique.
Description of drawings
Fig. 1 is A scheme steel plate of the present invention 1/4 place metallographic structure;
Fig. 2 is B scheme steel plate of the present invention 1/4 place metallographic structure;
Fig. 3 is C scheme steel plate of the present invention 1/4 place metallographic structure;
Fig. 4 is 630 ℃ of tempered steel sheet metals of A scheme of the present invention phase constitution;
Fig. 5 is 650 ℃ of tempered steel sheet metals of A scheme of the present invention phase constitution;
Fig. 6 is 680 ℃ of tempered steel sheet metals of A scheme of the present invention phase constitution;
Fig. 7 is 630 ℃ of tempered steel sheet metals of B scheme of the present invention phase constitution;
Fig. 8 is 650 ℃ of tempered steel sheet metals of B scheme of the present invention phase constitution;
Fig. 9 is 680 ℃ of tempered steel sheet metals of B scheme of the present invention phase constitution;
Figure 10 is 630 ℃ of tempered steel sheet metals of C scheme of the present invention phase constitution;
Figure 11 is 650 ℃ of tempered steel sheet metals of C scheme of the present invention phase constitution;
Figure 12 is 680 ℃ of tempered steel sheet metals of C scheme of the present invention phase constitution.
Embodiment
The actual chemical ingredients of the used steel of the embodiment of the invention: see Table 1
Table 1 chemical ingredients (wt%)
The temperature control heating is carried out in the steel billet shove charge.Steel plate rolling adopts two-stage controlled rolling process (recrystallization zone rolling+the non-recrystallization district is rolling), carries out online acceleration cooling after rolling, and speed of cooling is controlled at 25～35 ℃/S interval.Concrete rolling technology sees Table 2.Cooling back steel plate carries out rolling off the production line behind the aligning of hot straightening+heavily and carries out temper, and the steel plate tempering is carried out at roller hearth heat-treated furnace.Tempering temperature is controlled at 650～680 ℃ of intervals.
Each procedure technology parameter of table 2 actual measurement
Steel plate after Overheating Treatment, at wide 1/4 place of the plate of steel plate and thickness of slab 1/4 place sampling carry out the mother metal mechanical properties test, assay sees Table 3.
The mechanical property of table 3 steel plate TMCP state
The metallographic structure of TMCP state is observed: Fig. 1～Fig. 3 is the ferrite bainite tissue of very refinement.The check of steel plate TMCP+ Annealed Strip conventional mechanical property sees Table 4.
Table 4TMCP+ Annealed Strip steel plate mechanical property
Option A tempering attitude sample metallographic structure: Fig. 4～Fig. 6, after 630 ℃, 650 ℃, 680 ℃ insulations tempering in 90 minutes, ferrite bainite is organized alligatoring slightly, and the ferrite polygonization does not take place, and tissue is stable.
Option b tempering attitude sample metallographic structure: Fig. 7～Fig. 9, after 630 ℃, 650 ℃, 680 ℃ insulations tempering in 90 minutes, ferrite bainite is organized alligatoring slightly, and the ferrite polygonization does not take place, and tissue is stable.
Scheme C tempering attitude sample metallographic structure: Figure 10～Figure 12, after 630 ℃, 650 ℃, 680 ℃ insulations tempering in 90 minutes, ferrite bainite is organized alligatoring slightly, and the ferrite polygonization does not take place, and tissue is stable.
Claims (3)
1, a kind of high-temperature resistant tempered heavy plate with low susceptibility to welding crack, the weight percent that it is characterized in that the slab chemical ingredients is: C 0.08%～0.11%, Si 0.15%～0.40%, Mn 1.20%～1.75%, P≤0.020%, S≤0.006%, Ni 0.20%～0.45%, Cr 0.15%～0.30%, Mo 0.20%～0.40%, Cu 0.10%～0.30%, V 0.03%～0.06%, Nb 0.04%～0.06%, Als 0.025%～0.035%, Ti 0.015%～0.025%, surplus is Fe and unavoidable impurities, and chemical ingredients satisfies:
P
cm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.26％。
2, the production method of a kind of high-temperature resistant tempered heavy plate with low susceptibility to welding crack as claimed in claim 1 adopts the hot metal pretreatment technology, converter smelting, and LF stove+VD stove vacuum-treat, continuous casting and rolling technology is characterized in that:
1) Heating temperature before the hot rolling: billet heating temperature is 1150～1240 ℃;
2) rolling condition: adopt austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel billet soaking;
The austenite recrystallization district is rolling: the fs of controlled rolling, temperature range is at 1150～1000 ℃, and the single pass draft is greater than 10%, the cumulative deformation in this stage 〉=55%;
Austenite non-recrystallization district is rolling: the subordinate phase of controlled rolling, temperature range be controlled at≤940 ℃, and the single pass draft is greater than 10%, the cumulative deformation in this stage 〉=55%;
3) online pressure cooling: after hot rolling finishes, with temperature at Ar
3Above steel plate is forced cooling, and the water temp of going into of steel plate is 840～860 ℃, and the final cooling temperature of steel plate is controlled at 280～350 ℃, and the speed of cooling of steel plate is controlled at 25～35 ℃/S, the speed of cooling at thickness of slab 1/2 place 10 ℃/more than the S;
4) temper: 600～680 ℃ of tempering temperatures.
3, the production method of a kind of high-temperature resistant tempered heavy plate with low susceptibility to welding crack according to claim 1 is characterized in that, the thickness of steel plate is 12～40mm.
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| CN105112810A (en) * | 2015-09-07 | 2015-12-02 | 江阴兴澄特种钢铁有限公司 | Steel for high heat input resisting welding and preparation method thereof |
| CN108385020A (en) * | 2018-01-22 | 2018-08-10 | 五矿营口中板有限责任公司 | The high-strength steel sheet and its manufacturing method of 420MPa grades of low-welding crack-sensitives |
| CN113564461A (en) * | 2021-06-29 | 2021-10-29 | 鞍钢股份有限公司 | Austenitic stainless steel plate for fast neutron reactor and manufacturing method thereof |
| CN113564461B (en) * | 2021-06-29 | 2022-05-20 | 鞍钢股份有限公司 | Austenitic stainless steel plate for fast neutron reactor and manufacturing method thereof |
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Application publication date: 20100303 |