CN102953018A - High-strength pipeline steel, steel pipe and manufacture method thereof - Google Patents
High-strength pipeline steel, steel pipe and manufacture method thereof Download PDFInfo
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Abstract
The invention relates to a high-strength pipeline steel which comprises the following chemical components by weight percent: 0.01-0.12 % of C, 1.0-2.5 % of Mn, less than or equal to 0.6 % of Si, less than or equal to 0.0030 % of S, less than or equal to 0.015 % of P, 0.01-0.09 % of Nb, 0.0025-0.030 % of Ti, less than or equal to 0.08 % of Alt, less than or equal to 1.0 % of Mo, less than or equal to 1.2 % of Cu, less than or equal to 1.5 % of Ni, less than or equal to 1.2 % of Cr, less than or equal to 0.0030 % of B, less than or equal to 0.01 % of Ca, 0.001-0.010 % of N, and the balance being iron and unavoidable impurities. The steel is polygonal ferrite and bainite duplex structure. A manufacture method of the high-strength steel pipe comprises heating slab with a temperature of 1100 to 1250 DEG C, rolling a non-recrystallization region with a starting temperature of 750 to 920 DEG C and a terminating temperature of 720 to 840 DEG C, two-stage cooling under control with an ACC terminating cooling temperature of 200 to 580 DEG C and a cooling rate of 5 to 30 DEG C per second, and manufacturing the pipe by using a UOE technology with a compression rate of 0.1 to 0.5 % and a diameter-expanding rate of 0.5 to 1.5 %. The obtained steel pipe can meet demands of low yield ratio and high uniform elongation.
Description
Technical field
The present invention relates to pipe line steel, particularly relate to have low yield strength ratio, high uniform elongation high-strength line-pipe steel for steel pipes, steel pipe and manufacture method thereof.
Background technology
Along with the development of pipeline industry, length needs the special locations such as approach seismic zone, frozen soil layer apart from the oil and gas transport pipeline, and in order to guarantee the security of pipeline transportation, people begin to pay close attention to the anti-adaptability to changes of high-strength line-pipe steel in recent years.Traditional piping design is based on stress design, yet in the multiple district of the geologic hazards such as earthquake, pipeline will bear larger displacement strain, and pipeline failure is not only by stress control.Proposed the new ideas of " based on stress design " for this class pipe engineering, this type of pipe line steel has been required to have certain anti-adaptability to changes.Pipe line steel not only will satisfy the requirement of the transverse mechanical performance of " stress design " like this, the requirement that also will satisfy " stress design " is that the longitudinal stretching curve of steel plate has dome-type (Round house) feature, has simultaneously the characteristics such as low yield tensile ratio, high uniform elongation, High stress ratio.
JP2005-15823A discloses a kind of pipeline High Tensile Steel Tube and manufacture method thereof of deformation performance excellence.The yield strength of the length direction of this steel pipe is 70-95% with the ratio YSL/YSC of the yield strength of circumferential direction, it contains (quality %) C:0.03-0.12%, below the Si:0.8%, Mn:0.8-2.5% is below the P:0.03%, below the S:0.01%, below the Nb:0.01-0.1%, Ti:0.005-0.03% is below the Al:0.1%, N:0.001-0.008%, satisfy Ti-3.4N 〉=0, contain below the Ni:1%, below the Mo:0.6%, below the Cr:1%, below the Cu:1%, below the V:0.1%, below the Ca:0.01%, below the REM:0.02%, Mg:0.006% with lower a kind of or; Two kinds, remnants are iron and inevitable impurity.Microstructure is that ferrite and the remnants of 30-80% are that martensite and/or bainite consist of by area occupation ratio.Steel disc carries out hot rolling 950 ℃ of heating, below the air cooling to 500 ℃, reheats at 740-850 ℃, be cooled to below 400 ℃ with the speed of 10 ℃/s, and be tubular with steel plate forming, after the end welding with the docking section, carry out the expander of 0.8-3% and process.The Composition Design of this patent is for adding V, Mg and REM, and without the B element, and adopted steel plate heat treatment process.
JP 2004-124167A discloses a kind of have superior weldability energy and the high-strength line-pipe steel plate of deformability and the method for manufacturing of steel pipe.Adopt the low-carbon (LC) design on its composition, and add the alloying elements such as Mn, Nb, Ti, Ni, Cu, Cr, Mo, V and Mg; Adopt Ar
3Above temperature is opened cold TMCP technique, obtains acicular ferrite structure.Its Composition Design thinking (added V and Mg, and without the B element), and adopt Ar
3Above temperature is opened cold TMCP technique, and its microtexture type is acicular ferrite.
JP 2005-060839A discloses the method for manufacturing of the high-strength line-pipe steel pipe of a kind of low yield strength ratio, high tenacity, high strain aging resistance.Adopt the low-carbon (LC) design on its composition, be combined the precipitate that forms with C by Mo, Ti, V and realize reinforcement.Its Composition Design thinking (added V and do not add Cu, Ni, Cr), it adopts the production technique of on-line heating, and its microtexture type is bainite+horse island difficult to understand tissue.
JP 2006-283147A discloses a kind of method for manufacturing with high-strength line-pipe steel pipe of deformability and high corrosion resistance.Adopt the low-carbon (LC) thinking at Composition Design, add the alloying elements such as Mn-Ni-Cu-Mo-Nb-Ti, and set forth corresponding technique.Its Composition Design thinking (not containing Cr and B), its microtexture type are take acicular ferrite as main.
Along with pipeline is laid to the zone of this seismic zone and frozen soil layer gradually, cause the demand of anti-strain pipe line steel increasing.Recently, the anti-strain pipeline Weight of steel of having planned to lay just reaches millions of tons.For this reason, need a kind of requirement of not only satisfying the transverse mechanical performance of " stress design " of exploitation, also satisfy the requirement of " stress design ", the longitudinal stretching curve that is steel plate has cupola type feature, has simultaneously the high-strength line-pipe steel pipe of the characteristics such as low yield tensile ratio, high uniform elongation, High stress ratio.
Summary of the invention
The object of the present invention is to provide a kind of have low yield strength ratio, high uniform elongation high-strength line-pipe steel.
To achieve these goals, of the present invention have low yield strength ratio, a high uniform elongation high-strength line-pipe steel, its weight percent chemical composition is: C:0.01-0.12%, Mn:1.0-2.5%, Si≤0.6%, S≤0.0030%, P≤0.015%, Nb:0.01-0.09%, Ti:0.0025-0.030%, Alt≤0.08%, Mo≤1.0%, Cu≤1.2%, Ni≤1.5%, Cr≤1.2%, B≤0.0030%, Ca≤0.01%, N:0.001-0.010%, all the other are iron and inevitable impurity.
Preferably, C:0.01-0.10%.
Preferably, Mn:1.03-2.45%.
Preferably, Nb:0.015-0.085%.
Preferably, Ti:0.0025-0.020% or Ti:0.005-0.020%.
Preferably, Alt:0.02-0.08%.
Preferably, Mo:0.2-0.9%, more preferably, 0.2-0.6%.
Preferably, Cu:0.1-1.2%.
Preferably, Ni:0.1-1.4%.
Preferably, Cr:0.1-1.1%.
Preferably, B:0.0008-0.0028%.
Preferably, the high-strength line-pipe steel with low yield strength ratio, high uniform elongation of the present invention is polygonal ferrite+bainite duplex structure.
Preferably, polygonal ferrite accounts for approximately 50-75% in the microstructure of steel of the present invention.
Among the present invention, unless otherwise, content all refers to weight percent content.
Another object of the present invention provide have low yield strength ratio, the high-strength line-pipe of high uniform elongation is with the manufacture method of steel, the method comprises:
Converter or electrosmelting, external refining, continuous casting;
Heating of plate blank, slab heating temperature: 1100-1250 ℃;
Controlled rolling, wherein, the beginning temperature that non-recrystallization zone is rolling: 750-920 ℃, be preferably 780-920 ℃, stop rolling temperature: 720-840 ℃;
The two-stage control cooling, ACC (accelerating cooling) stops cooling temperature: 200-580 ℃, and speed of cooling is 5-30 ℃/s; Preferably, ACC termination cooling temperature is 200-400 ℃ or 300-500 ℃; Preferably, speed of cooling is 5-20 ℃/s or 20-30 ℃/s.
UOE (forming U shaped articles-O forming-hole enlargement (Expanding)) technique is carried out vertical masonry joint union-melt weld tubulation, and rate of compression is 0.1-0.5%, enlarging rate 0.5-1.5%.
The present invention is directed to microalloying polygonal ferrite+bainite duplex structure and have high strength, high tenacity and the good characteristics such as anti-strain property, take material reinforcement theories such as grain refining, phase transformation strengthening and dislocations strengthenings as the basis, adopted lower carbon content, super low sulfur, Nb, Ti, B microalloying in conjunction with the Composition Design of Cu, Ni, Cr, Mo alloying to the Composition Design of high-strength line-pipe steel pipe with polygonal ferrite+bainite duplex structure.The slab process using TMCP (the heat engine tool control technique) technology of controlled rolling+two-part control cooling, carry out the duplex structure control of the finished product by reasonable component and technique, with the polygonal ferrite that obtains to have low yield strength ratio, high uniform elongation+bainite duplex structure.
Not only can satisfy the requirement of the body lateral performance of " stress design " according to the pipeline steel tube of elemental composition design and processes of the present invention production, the requirement that also can satisfy " stress design " is that the longitudinal stretching curve of body has cupola type feature, has simultaneously low yield tensile ratio, high strain hardening index, the high characteristics such as uniform elongation.
Compare with the existing steel grade of producing, the performance of the pipeline steel tube of producing according to the present invention reaches following requirement:
Tensile property: the yield strength YS=485-690MPa of cross directional stretch, tensile strength TS=570-825MPa, yield tensile ratio YR≤0.88; The yield strength YS=450-630MPa of longitudinal stretching, tensile strength TS=570-775MPa, yield tensile ratio YR≤0.83, uniform elongation uEl 〉=8%.
The v-notch impact property: under test temperature-20 ℃, the ballistic work mean value 〉=250J of 10 * 10 * 55mm sample.
The DWTT performance: under the test temperature-20 ℃, average shear area SA% 〉=85%, single shear area SA% 〉=70%.
Description of drawings
Fig. 1 is the metallographic structure figure of the embodiment of the invention 1 steel plate.
Figure 2 shows that the longitudinal stretching curve of the embodiment of the invention 1 steel, wherein X-coordinate is strain (strain), and ordinate zou is stress (stress).
Embodiment
Below in conjunction with specific embodiment the present invention is described in detail.
High-strength line-pipe composition of steel with low yield strength ratio, high uniform elongation of the present invention is with low C, high Mn, by adding the microalloy elements such as micro-Nb, Ti, B, a small amount of Mo, Cr and Cu, Ni alloying element, in conjunction with slab controlled rolling+two stage type cooling technique, obtain polygonal ferrite+bainite duplex structure, have the performance of good anti-strain to guarantee pipe line steel.The Main Function of its fundamental element is as follows:
Carbon: be strengthening element most economical, the most basic in the steel, by solution strengthening and precipitation strength the intensity that improves steel there is obvious effect, but raising C content has negative impact to ductility, toughness and the weldability of steel, reduce the toughness that C content helps to improve steel on the one hand, can improve on the other hand the welding property of steel, but carbon content is crossed low meeting and is reduced grain-boundary strength, therefore control C content is 0.01-0.12% among the present invention, preferably, C content is 0.01-0.10%, and more preferably C content is 0.03-0.095%.
Silicon: be to have the effect that increases fluidity molten steel, need have certain Si content to union-melt weld, ferrite when Si promotes austenite in addition to ferrite transformation is simultaneously separated out, but too much Si easily makes steel plate form ferric oxide at high temperature, therefore, the Si content control of this steel grade is no more than 0.6%, is preferably 0.1-0.5%.
Manganese: improving the intensity of steel by solution strengthening, is the main and most economical strengthening element that compensation causes loss of strength in the pipe line steel because of the C content.Mn still enlarges the element of γ phase region, can reduce the γ of steel → α transformation temperature, helps to obtain tiny phase-change product, can improve steel toughness, reduce ductile-brittle transition temperature.Therefore, control Mn content is 1.0-2.5% among the present invention, is preferably 1.03-2.45%, more preferably 1.55-2.50%.
Niobium: be one of topmost element in the modern microalloying pipe line steel, fairly obvious to the effect of grain refining.Separate out the austenitic recovery and recrystallization of obstruction deformation by NbC strain inducing in the course of hot rolling, when making the rolling deformation austenite structure in non-recrystallization zone in phase transformation with the control cooling, controlled rolling changes tiny phase-change product into, so that steel has high strength and high tenacity.Cooperate suitable C content to improve the effect of the content performance NbC of Nb among the present invention, the addition of Nb is 0.01-0.09% for this reason, is preferably 0.015-0.085%.
Titanium: be strong solid N element, the stoichiometric ratio of Ti/N is 3.42, utilizes the Ti fixing following N of 60ppm in the steel just about 0.02%, can form the TiN precipitated phase of tiny high-temperature stable when sheet billet continuous casting.Austenite Grain Growth when this tiny TiN particle can effectively hinder slab and reheats, help to improve the solid solubility of Nb in austenite, simultaneously the impelling strength of improving welded heat affecting zone there is obvious effect, therefore, the content that adds Ti among the present invention is 0.0025-0.030%, be preferably 0.0025-0.02%, more preferably 0.005-0.02%.
Molybdenum: be to enlarge the γ phase region, separate out first ferrite when postponing γ → α phase transformation and form, promote the principal element that acicular ferrite forms, phase-change organization plays an important role to control, and selectivity is added Mo among the present invention, and the addition general control is below 1.0%.Preferably, add 0.2-0.9%, more preferably, the Mo that adds 0.2-0.6% under certain cooling conditions and termination rolling temperature in the Ultra-low carbon pipe line steel just can obtain obvious bainite type transmutation product, change to the low temperature direction because of phase transformation simultaneously, can make and organize further refinement, mainly be the intensity that improves steel by the phase transformation strengthening of tissue.
Chromium: improve material hardening capacity, can improve intensity and the hardness of steel, and make steel have good erosion resistance and and bad property of antioxygen.Control chromium content is below 1.2%, to be preferably 0.1-1.1% among the present invention.
Sulphur, phosphorus: be inevitable impurity element in the steel, it is more low better to wish.By super low sulfur (less than 30ppm) and Ca processing sulfide is carried out inclusion morphology control, can make pipe line steel have high toughness.Control S≤0.0030% among the present invention, P≤0.015%.
Copper, nickel: can improve by solution strengthening effect the intensity of steel, Cu also can improve the solidity to corrosion of steel simultaneously, and the adding of Ni mainly is to improve the red brittleness that Cu easily causes in steel, and useful to toughness.In thick specification pipe line steel, also can compensate the strength degradation that the increase because of thickness causes.Therefore, selectivity interpolation copper and mickel and addition are controlled at Cu≤1.2%, Ni≤1.5% among the present invention.Be preferably Cu:0.1-1.2%, Ni:0.1-1.4%.
Boron: the effect of boron in steel of the present invention: 1. improve the hardening capacity of steel, general add-on less (0.0003-0.0050%).2. improve the hot strength of steel, strengthen the effect of crystal boundary.Control B≤0.0030% among the present invention, preferred 0.0008-0.0028%.
Calcium: Ca is the inclusion shape for the control steel grade, adding by Ca can make the MnS that has high-temp plastic in the steel change the on-deformable CaS of high temperature or calcium-aluminate into, make steel billet be mingled with for spherical the transverse toughness that can significantly improve in high temperature rolling Sulfur During Process compound.Ca is also unsuitable too high, in order to avoid increase the content of inclusion.Be controlled at≤0.01%, preferred 0.0010-0.0050%.
Nitrogen: N is the inevitable impurity element of steel grade, and general control is below 0.01%.Preferably control less than 0.001-0.0080%.
Aluminium: the deoxidation products of steel is controlled at 0.02-0.08%.
According to the present invention, make by the following method the high-strength line-pipe steel pipe with low yield strength ratio, high uniform elongation:
Converter or electrosmelting, external refining, continuous casting;
Heating of plate blank, slab heating temperature: 1100-1250 ℃, can guarantee being solidly soluted in the austenite of alloying element, can avoid too growing up of austenite crystal again;
Controlled rolling, wherein, the beginning temperature that non-recrystallization zone is rolling: 750-920 ℃, be preferably 780-920 ℃, stop rolling temperature: 720-840 ℃, guarantee in the austenite one phase district rolling;
The two-stage control cooling, ACC stops cooling temperature: 200-580 ℃, and speed of cooling is 5-30 ℃/s, guarantees to obtain ferrite and bainite duplex structure, and the per-cent of second-phase;
UOE (forming U shaped articles-O forming-hole enlargement (Expanding)) technique is carried out vertical masonry joint union-melt weld tubulation, and rate of compression is 0.1-0.5%, enlarging rate 0.5-1.5%, the performance behind the assurance tubulation and the shape of welded tube.
Embodiment
Table 1 is depicted as the chemical composition of embodiments of the invention.
Table 2 and table 3 are depicted as the processing parameter of embodiments of the invention and the results of property of test.
Test example 1: tensile property
According to GB/T228 metallic substance tensile test at room temperature method (ISO 6892) each embodiment steel of the present invention is carried out tension test, its result such as table 2 and shown in Figure 2.
The yield strength YS=485-690MPa of the cross directional stretch of steel of the present invention, tensile strength TS=570-825MPa, yield tensile ratio YR≤0.88; The yield strength YS=450-630MPa of longitudinal stretching, tensile strength TS=570-775MPa, yield tensile ratio YR≤0.83, uniform elongation uEl 〉=8%.
Test example 2:V type notch shock performance
Than pendulum impact test method (ISO 148) various embodiments of the present invention are carried out the v-notch impact property according to the GB/T229 metallic substance summer and test, its result is as shown in table 2.
Steel of the present invention all satisfies test temperature-20 ℃, the requirement of the ballistic work mean value 〉=250J of 10 * 10 * 55mm sample.
Test example 3:DWTT performance
(API RP 5L3) carries out the DWTT performance test to the various embodiments of the present invention steel according to SY/T6476 conveying steel pipe Drop-Weight Tear Test (DWTT) method, and its result is as shown in table 2.
Steel of the present invention all satisfies under the test temperature-20 ℃, average shear area SA% 〉=85%, the requirement of single SA% 〉=70%.
Table 2
Table 3
SA1 is the shear area value of sample 1 in the table 3, and SA2 is the shear area value of sample 2.
Figure 1 shows that the metallographic structure of the embodiment of the invention 1 steel, from scheming the duplex structure that is organized as polygonal ferrite and bainite of visible steel of the present invention.
Other embodiment steel also can obtain metallographic structure similar to Example 1, are the duplex structure of polygonal ferrite and bainite.
Figure 2 shows that the longitudinal stretching curve of the embodiment of the invention 1 steel, wherein X-coordinate is strain (strain), and ordinate zou is stress (stress), is the dome-type stress strain curve as seen from Figure 2.
From above embodiment result as seen, not only can satisfy the requirement of the body lateral performance of " stress design " according to the pipeline steel tube of elemental composition design and processes of the present invention production, the requirement that also can satisfy " stress design " is that the longitudinal stretching curve of body has cupola type feature, has simultaneously low yield tensile ratio, high strain hardening index, the high characteristics such as uniform elongation.
Claims (17)
1. high-strength line-pipe steel, its weight percent chemical composition is: C:0.01-0.12%, Mn:1.0-2.5%, Si≤0.6%, S≤0.0030%, P≤0.015%, Nb:0.01-0.09%, Ti:0.0025-0.030%, Alt≤0.08%, Mo≤1.0%, Cu≤1.2%, Ni≤1.5%, Cr≤1.2%, B≤0.0030%, Ca≤0.01%, N:0.001-0.010%, all the other are iron and inevitable impurity.
2. high-strength line-pipe steel as claimed in claim 1 is characterized in that C:0.01-0.10%.
3. high-strength line-pipe steel as claimed in claim 1 or 2 is characterized in that Mn:1.03-2.45%.
4. such as the arbitrary described high-strength line-pipe steel of claim 1-3, it is characterized in that Nb:0.015-0.085%.
5. such as the arbitrary described high-strength line-pipe steel of claim 1-4, it is characterized in that Ti:0.0025-0.020% or Ti:0.005-0.020%.
6. such as the arbitrary described high-strength line-pipe steel of claim 1-5, it is characterized in that Alt:0.02-0.08%.
7. such as the arbitrary described high-strength line-pipe steel of claim 1-6, it is characterized in that, Mo:0.2-0.9%, preferably, 0.2-0.6%.
8. such as the arbitrary described high-strength line-pipe steel of claim 1-7, it is characterized in that Cu:0.1-1.2%.
9. such as the arbitrary described high-strength line-pipe steel of claim 1-8, it is characterized in that Ni:0.1-1.4%.
10. such as the arbitrary described high-strength line-pipe steel of claim 1-9, it is characterized in that Cr:0.1-1.1%.
11. such as the arbitrary described high-strength line-pipe steel of claim 1-10, it is characterized in that B:0.0008-0.0028%.
12. such as the arbitrary described high-strength line-pipe steel of claim 1-11, it is characterized in that, described steel is polygonal ferrite and bainite duplex structure.
13. high-strength line-pipe steel as claimed in claim 12 is characterized in that polygonal ferrite accounts for 50-75% in described duplex structure.
14. the steel pipe as the arbitrary described high-strength line-pipe of claim 1-13 is made of a steel is characterized in that the yield strength YS of cross directional stretch is 485-690MPa, tensile strength TS is 570-825MPa, yield tensile ratio YR≤0.88;
The yield strength YS of longitudinal stretching is 450-630MPa, and tensile strength TS is 570-775MPa, yield tensile ratio YR≤0.83, uniform elongation uEl 〉=8%;
V-notch ballistic work mean value 〉=250J of-20 ℃;
The DWTT performance: under the test temperature-20 ℃ test temperature, average shear area SA% 〉=85%, single shear area SA% 〉=70%;
Transverse cold bending performance: d=2a, 180 ° of crooked rear surface flawlesses.
15. the manufacture method of high-strength line-pipe steel pipe as claimed in claim 14 comprises:
Converter or electrosmelting, external refining, continuous casting;
Heating of plate blank, slab heating temperature: 1100-1250 ℃;
Controlled rolling, wherein, the beginning temperature that non-recrystallization zone is rolling: 750-920 ℃, stop rolling temperature: 720-840 ℃;
The two-stage control cooling, ACC stops cooling temperature: 200-580 ℃, and speed of cooling is 5-30 ℃/s;
UOE technique tubulation, rate of compression are 0.1-0.5%, enlarging rate 0.5-1.5%.
16. method as claimed in claim 15 is characterized in that, UOE technique is carried out vertical masonry joint union-melt weld tubulation.
17., it is characterized in that the beginning temperature that non-recrystallization zone is rolling: 780-920 ℃ such as claim 15 or 16 described methods.
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