CN103014553A - High-strength and high-toughness steel plate with 630 Mpa-level yield strength and preparation method of steel plate - Google Patents
High-strength and high-toughness steel plate with 630 Mpa-level yield strength and preparation method of steel plate Download PDFInfo
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Abstract
The invention relates to a high-strength and high-toughness steel plate, comprising the following chemical ingredients in percentage by weight: 0.035-0.06% of C, 0.15-0.30% of Si, 1.5-1.65% of Mn, not greater than 0.015% of P, not greater than 0.005% of S, 0.015-0.04% of Al, 0.035-0.045% of Nb, 0.01-0.02% of Ti, 0.20-0.40% of Cr, 0.20-0.30% of Mo, not greater than 0.25% of Ni, not greater than 0.006% of N, not greater than 0.004% of O, not greater than 0.005% of Ca, and the balance of iron and inevitable impurities, wherein Ca/s is not less than 1.5. A preparation method comprises the following steps of: heating a continuous casting blank or a steel blank at 150-1220 DEG C, and then performing multi-pass rolling on the continuous casting blank or the steel blank in an austenite recrystallization area and a non-recrystallization area, wherein the total reduction rate is not less than 70%, and the finish rolling temperature is not lower than 860 DEG C; rapidly carrying out water cooling on the rolled steel plate to a temperature range below Ms at a speed of 15-50 DEG C/s, and carrying out air cooling for 5-60 seconds; and conveying the cooled steel plate in an online induction heating furnace and rapidly heating the cooled steel plate to 555-615 DEG C at a speed of 1-10 DEG C/s, tempering for 40-60 seconds, and then discharging from a furnace and air-cooling. The obtained steel plate which is 10-25 mm thick has a longitudinal yield strength of not less than 630 MPa, a transversal yield strength of not less than 630 MPa, an elongation A50 of not less than 20%, and Akv of not less than 200 J at minus 60 DEG C, and is suitable for being used for preparing a long-distance conveying pipeline.
Description
Technical field
The present invention relates to a kind of pipeline conveying and use hot-rolled steel sheet, specifically relate to a kind of yield strength 630MPa grade high-strength high-tenacity pipeline and carry with steel plate and manufacture method thereof.
Background technology
In recent years, along with in the world long fast development apart from line of pipes, pipe line steel has become trend to high grade of steel development.Traditional X70, X80 can not meet the need of market.X90, X100, X120 even X140 have been among practicality or the research and development in the world now.Online thermal treatment (tempering) technique is except can shortened process, outside the saving energy, main is that original plate property with the TMCP explained hereafter is improved fully, particularly solve micro-alloyed steel owing to the rolling anisotropy that causes of non-recrystallization and the too high disadvantage of yield tensile ratio, thereby created condition for producing high grade pipeline steel plate.
At present, the patent that much relates to high Grade Pipeline Steel has been arranged both at home and abroad, disclose a kind of ultrahigh-intensity high-toughness X 120 pipe line steel and manufacture method thereof such as CN101165203A, its composition is: C:0.015-0.06%, Si≤0.6%, Mn:1.8-2.5%, P≤0.015%, S≤0.003%, Al≤0.06%, Nb:0.043-0.15%, Ti:0.005-0.03%, V≤0.15%, B:0.0005-0.030%, N≤0.012%, and Cu≤0.80%, Ni≤1.20%, Cr≤1.20%, two or more in Mo≤1.0%, 1100-1250 ℃ of heating, recrystallize 900-1200 ℃, non-recrystallize 720-940 ℃, finish to gauge 720-880 ℃, 3-30 ℃/s of cooling, cold 200-550 ℃ eventually, obtain being organized as the high-strength and high ductility X120 steel plate of bainite and martensite.
Present X90 rank and above high Grade Pipeline Steel, the alloying element of its interpolation is more, such as microalloy element Nb, generally adds more than 0.04%, may also will add certain V etc.; The precious alloy element is also high than the present invention as the interpolation of Cu, Ni, Cr and Mo in addition, so its carbon equivalent is high and weldability is undesirable.
Need also at present to provide that weldability improves is suitable for the high-intensity high-tenacity pipeline Plate Steel of long X90 grade of steel apart from line of pipes.
Summary of the invention
The object of the present invention is to provide a kind of yield strength the high-intensity high-tenacity pipeline steel more than 630MPa, particularly 10-25mm thickness steel plate.
For achieving the above object, the high-strength high-toughness steel plate of yield strength of the present invention more than 630MPa, the weight percent of its chemical composition is: C:0.035-0.06%, Si:0.15-0.30%, Mn:1.5-1.65%, P≤0.015%, S≤0.005%, Al:0.015-0.04%, Nb:0.035-0.045%, Ti:0.01-0.02%, Cr:0.20-0.40%, Mo:0.20-0.30%, Ni≤0.25%, N≤0.006%, O≤0.004%, Ca≤0.005%, Ca/S 〉=1.5, surplus is iron and inevitable impurity.
Preferably, C:0.035-0.059%.
Preferably, Si:0.20-0.30%.
Preferably, Mn:1.54-1.65%.
Preferably, P≤0.01%.
Preferably, S≤0.004%.
Preferably, Al:0.02-0.035%.
Preferably, Cr:0.24-0.36%.
Preferably, Mo:0.21-0.25%.
Preferably, Ni:0.18-0.22%.
Preferably, Nb:0.036-0.044%.
Preferably, Ti:0.012-0.019%.
Preferably, Ca≤0.0047%.
Preferably, N:0.003-0.005%, more preferably 0.003-0.004%.
Preferably, Ceq≤0.45.
Among the present invention, unless otherwise, content all refers to weight percentage.
Described steel plate be organized as bainite+martensite (may contain a small amount of residual austenite).
Another object of the present invention is to provide the manufacture method of described high-strength line-pipe steel steel plate, the method comprises:
Continuously cast bloom or steel billet carry out multi-pass rolling in austenite recrystallization district and non-recrystallization district after 1150-1220 ℃ of heating, total reduction 〉=70%, finishing temperature 〉=860 ℃;
Roll rear steel plate and be chilled to the following temperature range air cooling of Ms (Ms=561-474C-33Mn-17Cr-17Ni-21Mo) 5-60s with 15-50 ℃/s rapid water;
The steel plate of cooling enters online induction heater and quickly heats up to 555-615 ℃ of tempering 40-60s with 1-10 ℃/s, the air cooling of then coming out of the stove.
Preferably, in multi-pass rolling, recrystallization zone draft 〉=65%, non-recrystallization district draft 〉=50%.
Preferably, molten steel carries out continuous casting or die casting behind Fruit storage, need roll into through just steel billet after the die casting.
Preferably, finishing temperature is 860-900 ℃.
Preferably, roll rear steel plate and be chilled to 150-300 ℃ with 15-50 ℃/s rapid water.
The present invention obtains to be organized as bainite+tempered martensite (may contain a small amount of residual austenite) by suitable Composition Design and heating, rolling and roll rear quick cooling and online rapid heating short period of time tempering process.The 10-25mm Plate Steel is vertical, transverse yield strength 〉=630MPa, unit elongation A
50〉=20% ,-60 ℃ A
Kv〉=200J, cold-bending property is good, has satisfied pipeline conveying steel requirement.
Description of drawings
Fig. 1 is the metallographic structure photo of the 10mm Plate Steel of the embodiment of the invention 1.
Fig. 2 is the metallographic structure photo of the 25mm Plate Steel of the embodiment of the invention 4.
Embodiment
Below, by in conjunction with the embodiments characteristics of the present invention and effect being described in detail.
For yield strength the high-intensity high-tenacity pipeline steel more than 630MPa, the particularly purpose of 10-25mm thickness steel plate of providing of the present invention is provided, main chemical compositions is carried out following control:
Carbon: the key element of guaranteeing armor plate strength.General pipeline steel carbon content is less than 0.11%.Carbon improves armor plate strength by solid solution and precipitation strength, but carbon do obvious harm to toughness, plasticity and the weldability of steel, so the invariably accompany continuous reduction of carbon content of the development of pipe line steel.For the higher pipeline steel of toughness reguirements, general carbon content is lower than 0.08%.In order to obtain higher low-temperature impact toughness, the present invention adopts very low carbon content 0.035-0.06%, is preferably 0.035-0.059%.
Silicon: add silicon in the steel and can improve purity of steel and deoxidation.Silicon plays solution strengthening effect in steel.But the oxide skin viscosity when the too high meeting of silicone content makes the steel plate heating is larger, and the rear de-scaling difficulty of coming out of the stove causes rolling rear surface of steel plate red oxidization skin serious, and surface quality is relatively poor.And high silicon is unfavorable for welding property.Consider the impact of silicon each side, silicone content 0.15-0.30% is preferably 0.20-0.30% among the present invention.
Manganese: for the loss of strength that the reduction that compensates carbon content causes, improving manganese content is the most cheap direct way.But manganese has higher segregation tendency, so its content can not be too high, manganese content is no more than 2.0% in the general low-carbon micro steel-alloy.The add-on of manganese depends primarily on the intensity rank of steel.The content of manganese of the present invention should be controlled at 1.5-1.65%, is preferably 1.54-1.65%.
Sulphur and phosphorus: sulphur forms the plastic occluded foreignsubstance manganese sulfide with the chemical combination such as manganese in steel, especially unfavorable to horizontal plastic property and the toughness of steel, so the content of sulphur should be low as much as possible.Phosphorus also is the harmful element in the steel, the plasticity of grievous injury steel plate and toughness.For the present invention, sulphur and phosphorus all are inevitable impurity elements, should be more low better, consider the steel-making level of steel mill's reality, and the present invention requires P≤0.015%, and S≤0.005% is preferably P≤0.01%, S≤0.004%.
Aluminium: strong deoxidant element.Low as best one can in order to guarantee the oxygen level in the steel, the content of aluminium is controlled at 0.015-0.04%.Unnecessary aluminium and the nitrogen element in the steel can form the AlN precipitate after the deoxidation, improve intensity and the element autstenitic grain size of energy refinement steel when thermal treatment heat.Preferably, aluminium content is 0.02-0.035%.
Niobium: niobium is one of indispensable most important element of modern pipe line steel, can significantly improve recrystallization temperature and the crystal grain thinning of steel.The carbide strain inducing of niobium is separated out and can be hindered the austenitic Recovery and recrystallization of deformation in the course of hot rolling, and the deformation austenite structure after controlled rolling and control are cold obtains tiny phase-change product.Modern pipe line steel content of niobium is generally greater than 0.02%, and content of niobium is controlled at 0.035-0.045% among the present invention, is preferably 0.036-0.044%.
Titanium: titanium is carbide, and the Ti that adds trace in the steel is conducive to the N in the fixing steel, austenite crystal swell within reason when the TiN of formation can make heating steel billet, refinement original austenite grains degree.Titanium also can become TiC, TiS, Ti with carbon with the sulfuration symphysis respectively in steel
4C
2S
2Deng, they exist with the form of inclusion and second phase particles.These Carbonitride Precipitation things of titanium also can stop the heat affected zone grain growth when welding, improve welding property.Titanium content of the present invention is controlled at 0.01-0.02%, is preferably 0.012-0.019%.
Chromium: chromium improves the hardening capacity of steel, increases the temper resistance of steel.Chromium solubleness in austenite is very large, stable austenite, and a large amount of solid solutions in martensite after quenching, and in drawing process subsequently, can separate out Cr
23C
7, Cr
7C
3In carbide, improve intensity and the hardness of steel.In order to keep the intensity rank of steel, chromium can Partial Replacement manganese, weakens the segregation tendency of Gao Meng.Cooperate the online fast tiny Carbide Precipitation of induction heating tempering technology, alloy content that can corresponding reduction Nb therefore the present invention can add the chromium of 0.20-0.40%, is preferably 0.24-0.36%.
Molybdenum: molybdenum is crystal grain thinning significantly, improves intensity and toughness.Molybdenum can reduce the temper brittleness of steel, can also separate out very tiny carbide during simultaneously tempering, significantly strengthens the matrix of steel.Because molybdenum is very expensive strategic alloying element, so only add the molybdenum of 0.20-0.30% among the present invention, is preferably 0.21-0.25%.
Nickel: the element of stable austenite, to improving not significantly effect of intensity.Add nickel in the steel and especially in quenched and tempered steel, add especially low-temperature flexibility of toughness that nickel can significantly improve steel, simultaneously because nickel belongs to the precious alloy element, so alternative interpolation of the present invention is no more than 0.25% nickel element, preferably be no more than 0.22%.
Nitrogen: main and niobium is compounded to form niobium nitride or niobium carbonitrides precipitation strength at the pipeline nitrogen in steel.Effect for the inhibition recrystallize of bringing into play niobium, hope niobium when rolling suppresses recrystallize with the solid solution form, therefore general requirement is not added too much nitrogen in the pipe line steel, so that steel billet can most of dissolving at the carbonitride of (about 1200 ℃) niobium under the conventional heating temperature.Nitrogen content is no more than 60ppm in the general pipe line steel, preferred N≤0.005%, more preferably 0.003-0.004%.
Calcium: it mainly is to change oxide morphology that pipe line steel carries out that calcium processes, and that improves steel is thick in, lateral performance and cold-bending property.Also can not carry out calcium for the very low steel of sulphur content processes.The height of calcium contents of the present invention is decided on sulphur content, and Ca/S ratio 〉=1.5 are preferably Ca≤0.005%, more preferably Ca≤0.0047%.
Process for making is on the impact of product of the present invention:
Bessemerize and vacuum-treat: purpose is to guarantee the basal component requirement of molten steel, the obnoxious flavoures such as the oxygen in the removal steel, hydrogen, and add the necessary alloying element such as manganese, titanium, carry out the adjustment of alloying element.
Continuous casting or die casting: all even surface quality is good to guarantee the strand internal component, and the steel ingot of die casting need be rolled into steel billet.
Heating and rolling: continuously cast bloom or steel billet heat under 1150-1220 ℃ temperature, obtain uniform austenitizing tissue on the one hand, and the compound of the alloying elements such as niobium, titanium, chromium, molybdenum is partly dissolved.Carry out multi-pass rolling in austenite recrystallization district and non-recrystallization district, recrystallization zone draft 〉=65%, non-recrystallization district draft 〉=50%, total reduction 〉=70%, finishing temperature 〉=860 ℃, preferably, finishing temperature 860-900 ℃;
Fast cooling: roll rear steel plate and be chilled to Ms following (being preferably 150-300 ℃), then air cooling 5-60s with 15-50 ℃/s rapid water; In quick process of cooling, most alloying element is solidly soluted in the martensite.
Online tempering: the steel plate of cooling enters online induction heater and quickly heats up to 555-615 ℃ of tempering 40-60s with 1-10 ℃/s, the air cooling of then coming out of the stove.Tempering help to eliminate the fast internal stress that steel plate produces when cold and eliminate in the martensite packets or between tiny crack, the partially carbonized thing of disperse educt is strengthened, and is beneficial to simultaneously that not change austenitic transformation be bainite.
The present invention by suitable Composition Design, heating, controlled rolling, roll rear quick cooling and self-tempering, make steel plate realize refined crystalline strengthening, phase transformation strengthening, precipitation strength, intensity, the hardness of steel plate have been improved, has very high low-temperature flexibility, especially make steel plate obtain high yield strength, tissue is rendered as bainite+tempered martensite (may also contain a small amount of remaining A)+diffusion carbide to be strengthened.The 10-25mm Plate Steel is vertical, transverse yield strength 〉=630MPa, unit elongation A
50〉=20% ,-60 ℃ A
Kv〉=200J, cold-bending property is good, has satisfied the requirement of long-distance transport pipes with high Grade Pipeline Steel.
Embodiment
Embodiment 1
To smelt the molten steel of finishing by table 3 proportioning and behind Fruit storage, carry out continuous casting or die casting, slab thickness 80mm, the gained blank is after 1200 ℃ of heating, through multi-pass rolling, be rolled into the steel plate that thickness is 10mm in the austenite recrystallization temperature scope, total reduction is 88%, finishing temperature is 860 ℃, then with 35 ℃/s water-cooled to 250 ℃, quickly heat up to online 555 ℃ of tempering, then air cooling is to room temperature again;
The part steel plate metallographic structure of the present embodiment as shown in Figure 1.
The detailed composition of embodiment 2-5 sees Table 1, technological process such as embodiment 1, and processing parameter sees Table 2, and all embodiment gained plate properties see Table 3.
The chemical composition of table 1 embodiment of the invention 1-4, Ceq (wt%), Pcm
*Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/14
**Pcm＝C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B
Processing parameter and the steel plate thickness of table 2 embodiment of the invention 1-4
Test example 1: mechanical property
According to GB/T228-2002 metallic substance tensile test at room temperature method, GB 2106-1980 metal Charpy V test method, every mechanical property of GB/T 8363-2007 Drop-Weight Tear Test (DWTT) standard test embodiment of the invention 1-4 steel plate, it the results are shown in Table 3.
The mechanical property of table 3 steel plate of the present invention
E
Cvn-60 ℃:-60 ℃ of summers are than v-notch sample ballistic work
SA%
-15 ℃:-15 ℃ of DWTT fracture fracture surface of sample shear area
DWTT: Drop-Weight Tear Test (DWTT)
The 50%FATT:50% ductile-brittle transition temperature
Test example 2: bending property
According to GB/T 232-2010 bend test of metal materials method, embodiment of the invention 1-4 steel plate is carried out transverse cold bending d=2a, 180 ° of tests, the whole embodiment steel plates of its result are intact, all without surface crack.
Test example 3: metallographic structure
Fig. 1 is the metallographic structure figure of the 10mm Plate Steel of the embodiment of the invention 1.
Fig. 2 is the metallographic structure figure of the 25mm Plate Steel of the embodiment of the invention 4.
As seen from the figure, steel plate is organized as bainite and tempered martensite and possible a small amount of residual austenite.
Other embodiment also can obtain similar metallographic structure figure.
Can find out from above embodiment result, the present invention by suitable Composition Design, heating, controlled rolling, roll rear quick cooling and self-tempering, make steel plate realize refined crystalline strengthening, phase transformation strengthening, precipitation strength, intensity, the hardness of steel plate have been improved, has very high low-temperature flexibility, especially make steel plate obtain high yield strength, tissue is rendered as bainite+tempered martensite (may also contain a small amount of residual austenite)+diffusion carbide to be strengthened.The 10-25mm Plate Steel is vertical, transverse yield strength 〉=630MPa, unit elongation A
50〉=20% ,-60 ℃ A
Kv〉=200J, cold-bending property is good, has satisfied the requirement of long-distance transport pipes with high Grade Pipeline Steel.In addition, visible Ceq is lower and Pcm is lower from table 1, illustrates that the weldability of steel plate of the present invention and crack-resistance sensitivity are better.
Claims (22)
1. high-strength high-toughness steel plate, the weight percent of its chemical composition is: C:0.035-0.06%, Si:0.15-0.30%, Mn:1.5-1.65%, P≤0.015%, S≤0.005%, Al:0.015-0.04%, Nb:0.035-0.045%, Ti:0.01-0.02%, Cr:0.20-0.40%, Mo:0.20-0.30%, Ni≤0.25%, N≤0.006%, O≤0.004%, Ca≤0.005%, Ca/S 〉=1.5, surplus are iron and inevitable impurity.
2. high-strength high-toughness steel plate as claimed in claim 1 is characterized in that, C:0.035-0.059%.
3. high-strength high-toughness steel plate as claimed in claim 1 or 2 is characterized in that, Si:0.20-0.30%.
4. such as the arbitrary described high-strength high-toughness steel plate of claim 1-3, it is characterized in that Mn:1.54-1.65%.
5. such as the arbitrary described high-strength high-toughness steel plate of claim 1-4, it is characterized in that P≤0.01%.
6. such as the arbitrary described high-strength high-toughness steel plate of claim 1-5, it is characterized in that S≤0.004%.
7. such as the arbitrary described high-strength high-toughness steel plate of claim 1-6, it is characterized in that Al:0.02-0.035%.
8. such as the arbitrary described high-strength high-toughness steel plate of claim 1-7, it is characterized in that Cr:0.24-0.36%.
9. such as the arbitrary described high-strength high-toughness steel plate of claim 1-8, it is characterized in that Mo:0.21-0.25%.
10. such as the arbitrary described high-strength high-toughness steel plate of claim 1-9, it is characterized in that Ni:0.18-0.22%.
11. such as the arbitrary described high-strength high-toughness steel plate of claim 1-10, it is characterized in that Nb:0.036-0.044%.
12. such as the arbitrary described high-strength high-toughness steel plate of claim 1-11, it is characterized in that Ti:0.012-0.019%.
13. such as the arbitrary described high-strength high-toughness steel plate of claim 1-12, it is characterized in that Ca≤0.0047%.
14. such as the arbitrary described high-strength high-toughness steel plate of claim 1-13, it is characterized in that N:0.003-0.005%.
15. such as the arbitrary described high-strength high-toughness steel plate of claim 1-14, it is characterized in that Ceq≤0.45.
16. such as the arbitrary described high-strength high-toughness steel plate of claim 1-15, it is organized as bainite and martensite and possible a small amount of residual austenite.
17. such as the arbitrary described high-strength high-toughness steel plate of claim 1-16, its thickness is 10-25mm.
18. such as the arbitrary described high-strength high-toughness steel plate of claim 1-17, its vertical, transverse yield strength 〉=630MPa, unit elongation A
50〉=20% ,-60 ℃ A
Kv〉=200J.
19. the manufacture method such as the arbitrary described high-strength high-toughness steel plate of claim 1-18 comprises:
Continuously cast bloom or steel billet carry out multi-pass rolling in austenite recrystallization district and non-recrystallization district after 1150-1220 ℃ of heating, total reduction 〉=70%, finishing temperature 〉=860 ℃;
Roll rear steel plate and be chilled to the following temperature of Ms, air cooling 5-60s with 15-50 ℃/s rapid water;
The steel plate of cooling enters online induction heater and quickly heats up to 555-615 ℃ of tempering 40-60s with 1-10 ℃/s, the air cooling of then coming out of the stove;
Wherein, Ms=561-474C-33Mn-17Cr-17Ni-21Mo.
20. method as claimed in claim 19 is characterized in that, in the multi-pass rolling, and recrystallization zone draft 〉=65%, non-recrystallization district draft 〉=50%.
21. such as claim 19 or 20 described methods, it is characterized in that, finishing temperature is 860-900 ℃.
22. such as the arbitrary described method of claim 19-21, it is characterized in that, roll rear steel plate and be chilled to 150-300 ℃ with 15-50 ℃/s rapid water.
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| CN109482647A (en) * | 2018-10-31 | 2019-03-19 | 燕山大学 | Become the method that regulation improves material at low temperature toughness based on TSCR dynamic |
| CN113637922A (en) * | 2020-04-27 | 2021-11-12 | 宝山钢铁股份有限公司 | Economical low-yield-ratio high-strength steel and manufacturing method thereof |
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