CN101153370A - Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same - Google Patents
Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same Download PDFInfo
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Abstract
The invention provides a high strength low alloy steel plate suitable for high heat input welding and is characterized in that the chemical composition (wt percent) of steel comprises 0.04 percent to 0.16 percent of C, 0.10 percent to 0.50 percent of Si, 0.40 percent to 1.8 percent of Mn, 0.020 percent to 0.050 percent of Nb, 0.006 percent to 0.030 percent of Ti, 0.0030 percent to 0.010 percent of N, 0.015 percent to 0.060 percent of Al and the rest, Fe and other inevitable impurities; meanwhile, C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 is less than or equal to 0.45 percent and the total amount of Ti and the total amount of N are that [Ti percent]T is more than or equal to 2.667[N percent]T-0.004667 percent; moreover, Ti microalloying is adopted to ensure that the Ti/N ratio in the second sort of particle generated ranges between 2.4 and 3.2. The manufacture method of the steel plate adopts austenite recrystallization zone and austenite non-recrystallization zone rolling and forced water cooling after rolling; moreover, when the steel plate is under 50 KJ/cm to 150 KJ/cm high heat input welding, the welding heat affected zone has excellent toughness. The invention has the advantages of simple production process, low cost and wide applicability.
Description
Technical field
The invention belongs to low alloy steel and make the field, but the low-alloy high-strength steel plate and the manufacture method thereof of the welding of especially a kind of large-line energy.
Background technology
Before the present invention, the open report of some large-line energies with steel arranged.Patent " unmodified high-toughness low-temp steel for high-energy line welding and manufacture method thereof " (publication number CN1338528A) and " steel series with high linear energy and low weld crack sensitivity and production method thereof " (publication number CN1396294A) of declaring as Wuhan Iron and Steel Company.The common feature of these technology is to add B, utilizes the oxide compound of BN and Ca or Re to suppress the heat affected zone grain growth, improves the heat affected zone performance.But the adding of B often has side effects, and B is easy at crystal boundary poly-partially, causes the serious decline of base metal tenacity.Still there is not at present the good measure of carrying out B.In addition, the oxide compound of Ca, Re control is very difficult, when they when liquid state is separated out, grain growing is unrestricted, does not only have the effect that suppresses grain growth, also can destroy the toughness of mother metal.Therefore, this method is difficult to control aborning.
The patent " welded construction that is used for steel plate and manufacture method and this steel plate of use of the welded TiN+ZrN of having precipitated phase " (publication number CN1398302A) of Korea S Pu item company application obtains more TiN to stop the grain growth of heat affecting by the content that improves N, because it is very bad to the continuous casting performance impact of steel that N improves the back, the strand crackle is difficult to avoid, have to increase and ooze the N operation together, cause production technique and complexity thereof, production efficiency is low.
Summary of the invention
But the object of the present invention is to provide a kind of low-alloy high-strength steel plate and manufacture method thereof of large-line energy welding, base metal tenacity reduces, the incompatibility large-line energy requires and produce the unmanageable problem that goes up thereby solve.
The object of the present invention is achieved like this, but a kind of low-alloy high-strength steel plate of large-line energy welding, the chemical ingredients that it is characterized in that steel is (wt%): C:0.04%～0.16%, Si:0.10%～0.50%, Mn:0.40%～1.8%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%, Al:0.015%～0.060%.May contain Mo:0.08%～0.40%, Cu in addition :≤0.25%, V:0.02%～0.06%, Ni: one or more of≤0.8%, surplus are Fe and inevitably are mingled with.
For achieving the above object, the present invention also has the following feature:
1. adopt the Ti microalloying, make that the Ti/N ratio is between 2.4～3.2 in second particle of generation.
2. make Ti, N total content in the steel satisfy [Ti%] T 〉=2.667[N%] T-0.004667%.Thereby the solid solution in the assurance steel [N%]≤0.002% is improved the toughness of steel plate.
3. control carbon equivalent C
Eq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45% is to guarantee to have in the welded heat affecting zone tissue polygonal ferrite more than 15%.
The present invention adopts the reasons are as follows of mentioned component design:
C is the principal element of decision steel strength, also is the principal element of decision welded heat affecting zone tissue.When C is lower than 0.04%, be difficult to obtain needed intensity; When C is higher than 0.16%, the hardened structure of volume appears in the welded heat affecting zone, and make toughness obtain worsening, and be easy to generate welding crack during high C.C of the present invention is controlled at 0.04%～0.16%.
Si adds as deoxidant element, improves the intensity of steel plate simultaneously, influences the welding property of steel plate.Si is lower than at 0.10% o'clock, and deoxidation effect is poor, and surface of steel plate easily plays pit and red embroidery; But when Si greater than 0.50% the time, promote microstructure coarsening, and weld hot and cold crack sensitivity and all increase.Si of the present invention is controlled at 0.10%～0.50%.
Atomic radius and the Fe of Mn are close, form substitutional solid solution easily, are the elements of using maximum assurance armor plate strengths, also are the important elements that increases carbon equivalent.When Mn content was lower than 0.4%, intensity reduced, and the deleterious effect of Sization thing strengthens; When Mn content was higher than 1.8%, heat affected zone toughness degenerated.Mn of the present invention is controlled at 0.40%～1.8%.
Ti is the element that the present invention puts forth effort to study.Ti and N are combined into TiN, have the effect that the prevention austenite crystal is grown up and increased the ferrite forming core, can improve the toughness of heat affected zone effectively.The interpolation of Ti can also reduce the solid solution content of N, improves the aging performance of steel.The adding of Ti and N magnitude relation are very big.When Ti amount is lower than 2.667[N%] during T-0.004667%, solid solution N amount is more in the steel, and toughness and aging performance are all lower; When Ti/N is higher than 2.73, the alligatoring of TiN particle, to the beneficial effect weakening of heat affected zone, the Ti of solid solution simultaneously amount increases, the infringement base metal tenacity.Ti/N is between 2.4～3.2 in the control steel, and steel plate and welded heat affecting zone will have higher performance, exceed this scope, and significantly descending will appear in steel plate and welded heat affecting zone aspect of performance.Ti of the present invention is controlled at 0.006%～0.030%.
N is another element of putting forth effort to study of the present invention.N has two kinds of existing waies, and a kind of is solid solution, unfavorable to the mother metal performance, and another kind is to form the fine particle Nization thing that Mass distributes, and welding heat influence area toughness is had the improvement effect.The low then Nization thing quantity not sufficient of N amount is not suitable for the large-line energy welding.N amount height then solid solution N increases, and base metal tenacity and aging performance are bad, and continuously cast bloom is easy to generate crackle.N of the present invention is controlled at 0.003%～0.010%.
Nb can not only improve the recrystallization temperature of the operation of rolling, promotes the refined crystalline strengthening effect, can also form compound Nization thing with Ti, reduces the Ti/N ratio, improves the heat affected zone performance.In the present invention, in order to improve the intensity and the toughness of steel plate by thermo-mechanical rolling, must add the Nb of certain content.Nb measured low, was difficult for performance controlled rolling effect; Nb measures when excessive, promotes ferrite side plate to form in welding process, and is also unfavorable to toughness.Nb of the present invention is controlled at 0.020%～0.050%.
Al is main deoxidant element.When Al content is low, the deoxidizing capacity deficiency, Ti is oxidized and can not generate useful TiN particle; The Al too high levels forms macrobead easily and is mingled with.Al of the present invention is controlled at 0.015%～0.060%.Be easy to cause copper brittleness, cc billet surface quality problem;
P is an impurity element, increases the fragility of steel, should reduce as far as possible.But it is very high that metallurgy takes off the P cost, and being limited in can the guaranteed performance requirement below 0.015%.
S influences steel flexible principal element.In addition, when S content was high, sulfide can depend on TiN and grow up, and size of particles is increased, and the ability of pinning austenite grain boundary seriously undermines.Good take off the plasticity and toughness that S not only helps to improve steel plate, also help to control the size of TiN to suppress growing up of heat affected zone crystal grain.Therefore, satisfy the large-line energy welding requirements and must well take off S.The present invention requires S≤0.010%.
According to steel grade intensity and toughness reguirements, can add among Mo, Ni, V, the Cu one or more.The carbon equivalent but first three kind element is significantly increased causes hardenability to increase; Cu can improve the hardening capacity and the resistance to atmospheric corrosion of steel plate, but causes copper brittleness, cc billet surface quality problem easily.Therefore content must limit.The present invention requires that Mo satisfies 0.08%～0.40%, V satisfies 0.02%～0.06%, Cu≤0.25%, Ni≤0.8%.And satisfy C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45%.
Plate slab production stage of the present invention should comprise the converter smelting molten steel, and S is taken off in the LF refining, VD or RH vacuum-treat, and forging type can adopt die casting or continuous casting, but is good in the continuous casting mode.
Molten iron pre-desulfurization before the converter smelting, desulfurization slag will be taken off totally.Add Si, Mn in the converter stage and carry out a deoxidation.
The LF stove is made white slag, and the degree of depth is taken off S, the target component fine setting.In the deoxidation of LF refining stage secondary.
VD or RH refining, the treatment time was not less than 10 minutes, handled the back at Si-Ca and added Ti-Fe and Nb-Fe, blew Ar gas only 3 minutes, and is even to guarantee composition.Continuous casting superheating temperature≤25 ℃.
The principal character of this smelting technology is at first Mn, Si combined deoxidation, Al secondary deoxidation then, and the finishing operation before continuous casting adds Nb and Ti, and is not oxidized to guarantee Nb and Ti.Thereby in rolling and welding process, bring into play beneficial effect.
Concrete scheme of the present invention also comprises: the rolling method of producing steel plate according to mentioned component.
Steel plate rolling method of the present invention comprises manufacturing process such as soaking, roughing, finish rolling, acceleration cooling, aligning.
The present invention does not limit hot steel bloom or cold charge is gone into stove.But hot charging is save energy effectively, should preferentially use.
The Heating temperature of soaking is 1150～1200 ℃.
Rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel soaking of the present invention.
Roughing adopts the austenite recrystallization district rolling, and temperature range is between 1150～970 ℃, and every time draft is not greater than 10% (contain and adjust the dimensional precision passage), and this stage accumulation draft is greater than 50%.
Finish rolling adopts austenite non-recrystallization district rolling, 930～770 ℃ of temperature range controls.Every time draft is greater than 10% (do not contain and adjust the dimensional precision passage), the cumulative deformation in this stage 〉=55%.
Rolling the back adopts online laminar flow to quicken cooling.The water temp of going into of steel plate is 740～840 ℃, and the final cooling temperature of steel plate is controlled at 450～650 ℃, and the speed of cooling of steel plate is controlled at 4～20 ℃/s.
The present invention according to the carbon equivalent different mining of steel plate with different process for cooling to obtain required tissue and performances such as intensity, toughness.
When C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.36%, final cooling temperature is controlled at 500～650 ℃, and the speed of cooling of steel plate is controlled at 4～12 ℃/s, to obtain the tissue of ferrite, keeps steel plate that high toughness is arranged.Be lower than 4 ℃/s as speed of cooling, the ferrite grain size that obtains is more than 20 μ, and toughness is bad, and intensity is also lower.Be higher than 12 ℃/s as speed of cooling, then in tissue, obtain more bainite.
When 0.36%≤C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45%, final cooling temperature is controlled at 450～550 ℃, and the speed of cooling of steel plate is controlled at 8～20 ℃/s, to obtain the tissue of bainite, has good combination of strength and toughness.Be lower than 8 ℃/s as speed of cooling, obtain thick bainite and ferrite mixed structure, intensity and toughness are all undesirable.Be higher than 20 ℃/s as speed of cooling, then in tissue, obtain martensite.
Cooling back steel plate carries out on-line straightening, stacking slow cooling then.
The present invention adopts technique scheme can produce following beneficial effect:
1. the steel plate of pressing the present invention's production is when 50～150KJ/cm large-line energy welds, and welding heat influence area toughness is good.
2. chemical composition design is simple, and alloy addition level is few.Compare with conventional steel, under equality strength, by steel grade alloy coefficient (Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14) minimizing about 0.02～0.06% of the present invention's design.Both improve welding property, reduced production cost again.
3. adopt technologies such as austenite perfect recrystallization district+two stage controlled rollings in austenite non-recrystallization district, online laminar flow cooling, intensity and toughness are improved simultaneously, the steel plate of producing need not be heat-treated under the situation of low-alloy addition can satisfy performance requriements.
4. production technique of the present invention is easy, is fit to produce in batches operation.
Embodiment
Below will be by different embodiment and Comparative Examples the present invention relatively described.These embodiment only are the purposes that is used to explain, the present invention is not limited among these embodiment.
Table 1 is the chemical ingredients of each steel grade in embodiment and the comparative example.Every kind of steel capital is by converter smelting.Table 2 is the smelting condition of each steel grade in embodiment and the comparative example.Table 3 is the rolling technology of each steel grade in embodiment and the comparative example.Table 4 is the conventional mechanical property of each steel grade in embodiment and the comparative example.Table 5 is the welding property of each steel grade in embodiment and the comparative example.
By table 1～table 5 as seen, on same strength level, the steel plate that utilizes the present invention to produce has lower carbon equivalent, and heat affected zone toughness is also far above the contrast steel plate under the large-line energy welding conditions.
Table 1, the chemical ingredients of each steel grade in embodiment and the comparative example.(Wt，％)
| Steel grade | C | Si | Mn | P | S | Nb | V | Ti | Al | N | Mo | Cu | Ni | B | Ceq | Pcm |
| Embodiment 1 | .08 | 0.32 | 1.30 | .008 | .003 | .023 | -- | .009 | .038 | .0036 | -- | -- | -- | 0.310 | 0.156 | |
| Comparative Examples 1 | .15 | 0.33 | 1.40 | .007 | .005 | -- | -- | -- | .027 | .0063 | -- | -- | -- | 0.397 | 0.231 | |
| Embodiment 2 | .075 | 0.36 | 1.41 | .008 | .003 | .029 | -- | .014 | .042 | .0048 | -- | -- | -- | 0.325 | 0.158 | |
| Comparative Examples 2 | .013 | 0.35 | 1.51 | .008 | .005 | .018 | .017 | .020 | .030 | .0038 | -- | -- | -- | 0.397 | 0.219 | |
| Embodiment 3 | .08 | 0.48 | 1.49 | .008 | .003 | .035 | .032 | .015 | .035 | .0045 | -- | 0.10 | -- | -- | 0.346 | 0.177 |
| Comparative Examples 3 | .14 | 0.40 | 1.55 | .011 | .004 | .027 | .043 | .010 | .028 | .0064 | 0.15 | 0.29 | 0.10 | -- | 0.458 | 0.261 |
| Embodiment 4 | .08 | 0.25 | 1.50 | .009 | .003 | .040 | .040 | .014 | .037 | .0040 | 0.10 | 0.15 | -- | 0.368 | 0.162 | |
| Comparative Examples 4 | .07 | 0.27 | 1.56 | .012 | .005 | .022 | .020 | .008 | .026 | .0065 | 0.23 | 0.30 | 0.21 | .0015 | 0.405 | 0.200 |
Ceq＝C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14。
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B。
Table 2, the smelting condition of each steel grade in embodiment and the comparative example.(Wt，％)
| Steel grade | Refining unit | The deoxidation order | Nb adds the place | Ti adds the place |
| Embodiment 1 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 1 | LF | Mn、Si、Al | LF | LF |
| Embodiment 2 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 2 | LF+VD | Mn、Si、Al | LF | LF |
| Embodiment 3 | LF+RH | Mn、Si、Al | RH | RH |
| Comparative Examples 3 | RH+LF | Mn、Si、Al | RH | RH |
| Embodiment 4 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 4 | LF+VD | Mn、Si、Al | LF | LF |
Table 3, the rolling technology of each steel grade in embodiment and the comparative example.
| Steel grade | Finished product thickness mm | Heating temperature ℃ | Roughing start rolling temperature ℃ | Roughing finishing temperature ℃ | The total draft % of roughing | Finish rolling start rolling temperature ℃ | Finish rolling finishing temperature ℃ | The total draft % of finish rolling | Open cold temperature ℃ | Final cooling temperature ℃ | Speed of cooling ℃/s |
| Embodiment 1 | 45 | 1180 | 1120 | 987 | 60 | 890 | 840 | 58 | 825 | 600 | 5.5 |
| Comparative Examples 1 | 45 | 1182 | 1140 | 960 | 60 | --- | --- | 58 | --- | --- | --- |
| Embodiment 2 | 35 | 1176 | 1135 | 990 | 59 | 905 | 830 | 63 | 810 | 560 | 7 |
| Comparative Examples 2 | 35 | 1185 | 1130 | 984 | 59 | 930 | 850 | 63 | --- | --- | --- |
| Embodiment 3 | 32 | 1179 | 1120 | 980 | 67 | 910 | 815 | 58 | 800 | 520 | 9 |
| Comparative Examples 3 | 32 | 1186 | 1135 | 1010 | 67 | 920 | 820 | 58 | 810 | 580 | 6 |
| Embodiment 4 | 28 | 1183 | 1130 | 995 | 67 | 925 | 800 | 64 | 785 | 475 | 14 |
| Comparative Examples 4 | 28 | 1182 | 1140 | 1000 | 67 | 930 | 820 | 64 | 800 | 550 | 11 |
Table 4, the conventional mechanical property of each steel grade in embodiment and the comparative example.
| Steel grade | R el MPa | R m MPa | A ％ | Test temperature ℃ | AKv J | ||
| Embodiment 1 | 390 | 475 | 31.5 | -20 | 370 | 345 | 364 |
| Comparative Examples 1 | 365 | 470 | 32 | -20 | 283 | 294 | 315 |
| Embodiment 2 | 450 | 495 | 34 | -20 | 297 | 330 | 322 |
| Comparative Examples 2 | 430 | 500 | 31 | -20 | 305 | 265 | 277 |
| Embodiment 3 | 540 | 580 | 26 | -40 | 288 | 286 | 274 |
| Comparative Examples 3 | 490 | 560 | 23.5 | -40 | 220 | 283 | 245 |
| Embodiment 4 | 565 | 635 | 22 | -40 | 282 | 263 | 290 |
| Comparative Examples 4 | 520 | 615 | 19 | -40 | 212 | 226 | 208 |
Table 5, the welding joint mechanical property of each steel grade in embodiment and the comparative example.
| Steel grade | Welding process | Weld heat input KJ/cm | R m MPa | Test temperature ℃ | Heat affected zone AKv J | ||
| Embodiment 1 | Electro-gas (enclosed) welding | 256 | 475 | -20 | 256 | 256 | 282 |
| Comparative Examples 1 | Electro-gas (enclosed) welding | 220 | 470 | -20 | 174 | 163 | 164 |
| Embodiment 2 | Union-melt weld | 75 | 495 | -20 | 316 | 300 | 247 |
| Comparative Examples 2 | Union-melt weld | 75 | 500 | -20 | 132 | 72 | 45 |
| Embodiment 3 | Electro-gas (enclosed) welding | 151 | 580 | -40 | 215 | 210 | 233 |
| Comparative Examples 3 | Electro-gas (enclosed) welding | 155 | 560 | -40 | 99 | 16 | 38 |
| Embodiment 4 | Electro-gas (enclosed) welding | 144 | 635 | -40 | 210 | 125 | 156 |
| Comparative Examples 4 | Electro-gas (enclosed) welding | 140 | 615 | -40 | 47 | 30 | 37 |
Claims (4)
1. but the low-alloy high-strength steel plate of large-line energy welding, the chemical ingredients that it is characterized in that steel is (wt%): C:0.04%～0.16%, Si:0.10%～0.50%, Mn:0.40%～1.8%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%, Al:0.015%～0.060%, surplus is Fe and inevitably is mingled with, also should satisfy C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45% and total Ti content and total N content and meet [Ti%]
T〉=2.667[N%]
T-0.004667%, and adopt the Ti microalloying, make that the Ti/N ratio is 2.4～3.2 in second particle of generation.
2. but the low-alloy high-strength steel plate of a kind of large-line energy welding according to claim 1 is characterized in that containing Mo:0.08%～0.40%, Cu :≤0.25%, V:0.02%～0.06%, Ni: one or more of≤0.8%.
3. but manufacture method with the low-alloy high-strength steel plate of the described large-line energy of claim 1～2 welding, adopt austenite recrystallization district and austenite non-recrystallization district two stage rolling after it is characterized in that to contain the steel billet soaking of above-mentioned chemical ingredients, carry out Forced water cooling after rolling.
4. but the manufacture method of the low-alloy high-strength steel plate of a kind of large-line energy welding according to claim 3 is characterized in that billet heating temperature is 1150～1200 ℃; Roughing adopts the austenite recrystallization district rolling, and temperature range is between 1150～970 ℃, and every time draft is greater than 10%, and this stage accumulation draft is greater than 50%; Finish rolling adopts austenite non-recrystallization district rolling, 930～770 ℃ of temperature range controls, and every time draft is greater than 10%, the cumulative deformation in this stage 〉=55%; Roll the back and adopt online laminar flow to quicken cooling, the water temp of going into of steel plate is 740～840 ℃, and the final cooling temperature of steel plate is controlled at 450～650 ℃, and the speed of cooling of steel plate is controlled at 4～20 ℃/s.
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