CN102560254B - Low-Bauschinger-effect low-strain-aging-effect steel tube and manufacturing method thereof - Google Patents
Low-Bauschinger-effect low-strain-aging-effect steel tube and manufacturing method thereof Download PDFInfo
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- CN102560254B CN102560254B CN201210018129.6A CN201210018129A CN102560254B CN 102560254 B CN102560254 B CN 102560254B CN 201210018129 A CN201210018129 A CN 201210018129A CN 102560254 B CN102560254 B CN 102560254B
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Abstract
The invention belongs to the field of steel materials and manufacturing thereof, and discloses a low-Bauschinger-effect low-strain-aging-effect steel tube and a manufacturing method thereof. The steel tube comprises the following components in percentage by mass: 0.02-0.06% of C, 0.05-0.42% of Si, 1.61-1.99% of Mn, at most 0.020% of P, at most 0.010% of S, at most 0.11% of Nb, at most 0.06% of V, at most 0.05% of Ti, 0.0010-0.0080% of N, at most 0.50% of Cu, 0.60-1.00% of Cr, at most 0.0105 of Ca and the balance of Fe and inevitable impurities. The formula and the manufacturing method are reasonably designed; and the steel tube has low Bauschinger effect and low strain aging effect, and remains well matching of excellent deformability and excellent toughness.
Description
Technical field
The invention belongs to ferrous materials and manufacturing technology field thereof, be specifically related to steel pipe and the manufacture method thereof of a kind of low Bauschinger effect and low strain aging effect.
Background technology
Pipeline transportation is most economical, the most rational mode of oil and natural gas transportation.In recent years, along with developing rapidly of the oil and gas pipes technology of China, reach advanced world standards in the engineering practice aspect of high-pressure delivery and high grade of steel welded tube.Along with planning and the construction of lot of domestic and foreign sport pipework, the laying Service Environment of pipeline will be day by day cruel, to the demand of the gross distortion pipe line steel based on stress design, can get more and more.The high value added products such as exploitation gross distortion pipe line steel have caused domestic concern, and this can promoting enterprise technological transformation, product up-gradation.The production domesticization that realizes gross distortion pipe line steel has considerable Social benefit and economic benefit.
Yield strength is to describe an important parameter of pipe line steel mechanical property, but makes in the process of steel pipe when steel plate, can steel pipe yield strength be reduced owing to there is Bauschinger effect, performance inconsistency lattice.Bauschinger effect is the universal phenomenon that metallic substance has, i.e., after the micro-viscous deformation of pre-loaded generation, oppositely load yield strength and reduce.Existing research shows that Bauschinger effect size is mainly that chemical composition, grain fineness number, precipitate and the dislocation etc. that are subject to steel affect.In forming process, can there are two kinds of mechanism of strain hardening and Bauschinger effect in steel pipe, strain hardening improves yield strength, and Bauschinger effect reduces yield strength, and two kinds of mechanism are vied each other and made yield strength or rising or the reduction after tubulation.
Transportation pipe line adopts technology for external corrosion-proofing to carry out exterior coating rotproofing to steel pipe conventionally.In coating antiseptic technological process, adopt Frequency Induction Heating, make steel pipe surface surface temperature reach 200 ~ 250 ℃, epoxy powder, glue bond, polyethylene are melted and adhere to steel tube surface.Shot Blasting before steel tube forming, hole enlargement and rotproofing makes pipe line steel produce viscous deformation, and in steel pipe anticorrosive layer coating process afterwards, be subject to higher than 200 ℃ of above temperature impacts, thereby easily bring out strain aging, the yield tensile ratio of steel pipe is raise, homogeneous deformation elongation reduces, toughness declines, thereby makes deformability variation.
Therefore, in steel, Bauschinger effect can make the strength decreased of steel after tubulation, and strain aging effect can make the deformability of steel pipe decline.
Summary of the invention
The object of the present invention is to provide steel pipe and the manufacture method thereof of a kind of low Bauschinger effect and low strain aging effect.
For achieving the above object, the technical scheme that the present invention takes is as follows:
The steel pipe of a kind of low Bauschinger effect and low strain aging effect: the component of this steel pipe and mass percent are: C 0.02 ~ 0.06%, Si 0.05 ~ 0.42%, Mn 1.61 ~ 1.99%, P≤0.020%, S≤0.010%, Nb≤0.11%, V≤0.06%, Ti≤0.05%, N 0.0010 ~ 0.0080%, Cu≤0.50%, Cr 0.60 ~ 1.00%, Ca≤0.010%, surplus is Fe and inevitable impurity.
Further optimize, the component of this steel pipe and mass percent are: C 0.02 ~ 0.04%, Si 0.05 ~ 0.30%, Mn 1.61 ~ 1.91%, P≤0.010%, S≤0.005%, Nb≤0.11%, V≤0.06%, Ti≤0.030%, N 0.0010 ~ 0.0060%, Cu≤0.50%, Cr 0.61 ~ 0.90%, Ca≤0.008%, surplus is Fe and inevitable impurity.
The preparation method who the invention provides two kinds of steel pipes, is specially:
First method, comprises following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate (acicular ferrite structure) of described each component and mass percent;
B) steel plate is adopted JCO technique (" J " be shaped+" C " be shaped+" O " shaping) be shaped as steel pipe;
C) adopt vertical masonry joint submerged arc welding;
D) only the body beyond steel pipe seam is heated to austenite and adds 700 ~ 900 ℃ of ferrite two-phase regions, soaking time is 6 ~ 15min, and the speed cool to room temperature with 10 ~ 50 ℃/s, obtains ferrite and add martensite/bainite structure;
E) carry out hole enlargement;
F) apply processing.
Preferably, in step (b), JCO process forming step number is 11 ~ 21; In step (c), during welding, weld heat input is 10 ~ 60kJ/cm, and welding speed is 1.00 ~ 2.00m/min; In step (e), hole enlargement amount is 0.5 ~ 1.5%; In step (f), application temperature is 170 ~ 300 ℃.
Second method, comprises following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate (acicular ferrite structure) of described each component and mass percent;
B) steel plate is heated to austenite and adds 700 ~ 900 ℃ of ferrite two-phase regions, soaking time is 6 ~ 15min, and the speed cool to room temperature with 10 ~ 50 ℃/s, obtains ferrite and add martensite/bainite structure;
C) steel plate is adopted JCO technique (" J " be shaped+" C " be shaped+" O " shaping) be shaped as steel pipe;
D) adopt vertical masonry joint submerged arc welding;
E) carry out hole enlargement;
F) apply processing.
Preferably, in step (c), JCO process forming step number is 11 ~ 21; In step (d), during welding, weld heat input is 10 ~ 60kJ/cm, and welding speed is 1.00 ~ 2.00m/min; In step (e), hole enlargement amount is 0.5 ~ 1.5%; In step (f), application temperature is 170 ~ 300 ℃.
Steel C of the present invention and N content are lower, obviously reduce the strain aging effect of steel.Steel of the present invention does not add expensive Mo and Ni element, and cost is lower.Steel of the present invention increases the hardening capacity of steel by improving Cr, Mn content, in heat treatment process, lower cooling rate just can obtain ferrite and adds martensite/bainite duplex structure, has excellent deformation performance, and the while has also met the requirement of strength of steel.Steel of the present invention does not add B, and thermomechanical cooling controlling and rolling controlling process is easily prepared into acicular ferrite pipe line steel plate, and this tissue makes steel have excellent performance as critical zone tissue in heat treated early stage.
Before steel of the present invention critical zone thermal treatment, be organized as acicular ferrite structure, average grain diameter is less than 10 μ m, and intracrystalline has high density dislocation, and crystal grain distributes in the mixed and disorderly mode of random orientation.At the non-recrystallization zone of During Controlled Rolling rolling sequence, Nb, Ti segregation in deformed matrix makes recrystallize be difficult to carry out with separating out, after finish to gauge, in steel, there is a large amount of deformation bands, dislocation and microalloy element precipitate, become the effective forming core core of acicular ferrite, significantly crystal grain thinning.After critical zone thermal treatment insulating process in, austenite is forming core on acicular ferrite crystal boundary, intracrystalline lath circle and carbide, carbonitride, it is tiny, even that more austenite core distributes austenite, the grow up diffusion length of required C of austenite is less, be conducive to carbon in ferrite and spread and enrichment to austenite, the C of solid solution simultaneously, N continue carbide precipitate in the insulating process of critical zone.Above factor reduces solid solution C in the ferrite of steel of the present invention, N content, and anti-strain aging ability strengthens, and after coating, excellent deformability is kept.
The ferrite that is organized as after steel of the present invention critical zone thermal treatment adds martensite/bainite duplex structure, and the type organization steel has excellent deformation performance and obdurability combination.First method, steel formability and be welded into steel pipe after carry out again critical zone thermal treatment, whole body is ferrite and adds martensite/bainite duplex structure, there is not softened zone, and critical zone heat treatment process is discharged the deformation stress of steel pipe, strain aging effect and Bauschinger effect further reduce, and the performance of steel pipe is more superior.Second method, first steel plate is heat-treated to duplex structure by critical zone, after vertical masonry joint submerged arc welding near heat affected zone the martensite/bainite generation Recovery and recrystallization in body, strength decreased, this is the disadvantage of the method, but steel plate hot is processed, do not need the extra expensive equipment that adds, the existing equipment for Heating Processing of factory just can realize.
The ferrite of manufacture of the present invention adds martensite/bainite gross distortion pipe line steel stress strain curve and is " dome-type ", has higher initial strain hardening rate and strain-hardening index, and after tubulation, yield strength obviously increases.
Formula of the present invention and manufacture method are reasonable in design, and after tubulation, Bauschinger effect is low, and strain aging effect is low, make it still keep excellent deformation performance and excellent combination of strength and toughness.
Accompanying drawing explanation
Fig. 1 is embodiment 1 gained acicular ferrite structure photo;
Fig. 2 is that embodiment 1 gained ferrite adds martensite/bainite structure photo.
Embodiment
Below in conjunction with specific embodiment, technical scheme of the present invention is described in further detail, but protection scope of the present invention is not limited to this:
A steel pipe for low Bauschinger effect and low strain aging effect, the component of this steel pipe and mass percent are in Table 1.
Manufacture method:
First method, comprises following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate of described each component and mass percent, what now obtain is acicular ferrite structure's (Fig. 1 sees in the acicular ferrite structure of embodiment 1);
B) steel plate is adopted JCO process forming become steel pipe;
C) adopt vertical masonry joint submerged arc welding;
D) only the body beyond steel pipe seam being heated to critical zone--austenite adds 700 ~ 900 ℃ of ferrite two-phase regions, soaking time is 6 ~ 15min, with the speed cool to room temperature of 10 ~ 50 ℃/s, obtain ferrite and add martensite/bainite structure (ferrite of embodiment 1 adds martensite/bainite structure and sees Fig. 2);
E) carry out hole enlargement;
F) apply processing.
Second method, comprises following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate of described each component and mass percent, what now obtain is acicular ferrite structure;
B) steel plate being heated to critical zone--austenite adds 700 ~ 900 ℃ of ferrite two-phase regions, and soaking time is 6 ~ 15min, and the speed cool to room temperature with 10 ~ 50 ℃/s, obtains ferrite and add martensite/bainite structure;
C) steel plate is adopted JCO process forming become steel pipe;
D) adopt vertical masonry joint submerged arc welding;
E) carry out hole enlargement;
F) apply processing.
The tube-making process parameter of above-mentioned two kinds of methods is in Table 2, and method 1 is consistent with the processing parameter of method 2, and method 1 is the postheat treatment that is first shaped, and method 2 is first thermal treatment postforming.The performance of steel pipe is in Table 3.From table 3, the endwise tensile strength R of steel pipe
mbe greater than 570MPa, longitudinally yield tensile ratio R
t0.5/ R
mbe less than 0.86, homogeneous deformation elongation is greater than 6%, and stress strain curve shape is " dome-type " ,-5 ℃ of horizontal Charpy-V impact power A of lower tube body
kvbe greater than 160J, the obdurability of steel pipe and deformation performance are excellent, illustrate that strain aging effect and Bauschinger effect are less to the disadvantageous effect of steel tube performance.Method 1 steel formability and be welded into steel pipe after carry out again critical zone thermal treatment, near weld seam, there is not softened zone, and critical zone heat treatment process is discharged the deformation stress of steel pipe, compare with method 2, strain aging effect and Bauschinger effect further reduce, therefore, the steel pipe that tensile strength, impelling strength, homogeneous deformation elongation are all prepared higher than method 2, and there is lower yield tensile ratio.
Claims (6)
1. the manufacture method of a low Bauschinger effect and low strain aging effect steel pipe, the component of this steel pipe and mass percent are: C 0.02 ~ 0.06%, Si 0.05 ~ 0.42%, Mn 1.61 ~ 1.99%, P≤0.020%, S≤0.010%, Nb≤0.11%, V≤0.06%, Ti≤0.05%, N 0.0010 ~ 0.0080%, Cu≤0.50%, Cr 0.60 ~ 1.00%, Ca≤0.010%, surplus is Fe and inevitable impurity, it is characterized in that comprising following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate of described each component and mass percent;
B) steel plate is adopted JCO process forming become steel pipe;
C) adopt vertical masonry joint submerged arc welding;
D) only the body beyond steel pipe seam is heated to 700 ~ 900 ℃, soaking time is 6 ~ 15min, with the speed cool to room temperature of 10 ~ 50 ℃/s;
E) carry out hole enlargement;
F) apply processing.
2. manufacture method as claimed in claim 1, it is characterized in that: the component of this steel pipe and mass percent are: C 0.02 ~ 0.04%, Si 0.05 ~ 0.30%, Mn 1.61 ~ 1.91%, P≤0.010%, S≤0.005%, Nb≤0.11%, V≤0.06%, Ti≤0.030%, N 0.0010 ~ 0.0060%, Cu≤0.50%, Cr 0.61 ~ 0.90%, Ca≤0.008%, surplus is Fe and inevitable impurity.
3. manufacture method as claimed in claim 1 or 2, is characterized in that: in step (b), JCO process forming step number is 11 ~ 21; In step (c), during welding, weld heat input is 10 ~ 60kJ/cm, and welding speed is 1.00 ~ 2.00m/min; In step (e), hole enlargement amount is 0.5 ~ 1.5%; In step (f), application temperature is 170 ~ 300 ℃.
4. the manufacture method of a low Bauschinger effect and low strain aging effect steel pipe, the component of this steel pipe and mass percent are: C 0.02 ~ 0.06%, Si 0.05 ~ 0.42%, Mn 1.61 ~ 1.99%, P≤0.020%, S≤0.010%, Nb≤0.11%, V≤0.06%, Ti≤0.05%, N 0.0010 ~ 0.0080%, Cu≤0.50%, Cr 0.60 ~ 1.00%, Ca≤0.010%, surplus is Fe and inevitable impurity, it is characterized in that comprising following steps:
A) through hot metal pretreatment, smelting, refining, continuous casting and thermomechanical controlled rolling and controlled cooling process, prepare the steel plate of described each component and mass percent;
B) steel plate is heated to 700 ~ 900 ℃, soaking time is 6 ~ 15min, with the speed cool to room temperature of 10 ~ 50 ℃/s;
C) steel plate is adopted JCO process forming become steel pipe;
D) adopt vertical masonry joint submerged arc welding;
E) carry out hole enlargement;
F) apply processing.
5. manufacture method as claimed in claim 4, it is characterized in that: the component of this steel pipe and mass percent are: C 0.02 ~ 0.04%, Si 0.05 ~ 0.30%, Mn 1.61 ~ 1.91%, P≤0.010%, S≤0.005%, Nb≤0.11%, V≤0.06%, Ti≤0.030%, N 0.0010 ~ 0.0060%, Cu≤0.50%, Cr 0.61 ~ 0.90%, Ca≤0.008%, surplus is Fe and inevitable impurity.
6. the manufacture method as described in claim 4 or 5, is characterized in that: in step (c), JCO process forming step number is 11 ~ 21; In step (d), during welding, weld heat input is 10 ~ 60kJ/cm, and welding speed is 1.00 ~ 2.00m/min; In step (e), hole enlargement amount is 0.5 ~ 1.5%; In step (f), application temperature is 170 ~ 300 ℃.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101906568A (en) * | 2010-08-12 | 2010-12-08 | 中国石油天然气集团公司 | High-grade large-strain pipeline steel and manufacturing method of steel pipe |
| CN101914723A (en) * | 2010-08-30 | 2010-12-15 | 南京钢铁股份有限公司 | Hot-rolling large-deformation-resistance pipeline steel and preparation method thereof |
| CN102242311A (en) * | 2011-08-10 | 2011-11-16 | 中国石油天然气集团公司 | Crack initiation steel pipe for full-scale gas bursting test of large-diameter high-grade steel gas pipeline and preparation method thereof |
| CN102248023A (en) * | 2011-08-05 | 2011-11-23 | 中国石油集团渤海石油装备制造有限公司 | Method for manufacturing X70 steel-level large deformation-resistant longitudinally submerged arc welding pipe |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101906568A (en) * | 2010-08-12 | 2010-12-08 | 中国石油天然气集团公司 | High-grade large-strain pipeline steel and manufacturing method of steel pipe |
| CN101914723A (en) * | 2010-08-30 | 2010-12-15 | 南京钢铁股份有限公司 | Hot-rolling large-deformation-resistance pipeline steel and preparation method thereof |
| CN102248023A (en) * | 2011-08-05 | 2011-11-23 | 中国石油集团渤海石油装备制造有限公司 | Method for manufacturing X70 steel-level large deformation-resistant longitudinally submerged arc welding pipe |
| CN102242311A (en) * | 2011-08-10 | 2011-11-16 | 中国石油天然气集团公司 | Crack initiation steel pipe for full-scale gas bursting test of large-diameter high-grade steel gas pipeline and preparation method thereof |
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