CN101451217A - Steel for pipeline and method for producing the same - Google Patents
Steel for pipeline and method for producing the same Download PDFInfo
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- CN101451217A CN101451217A CNA2007101805972A CN200710180597A CN101451217A CN 101451217 A CN101451217 A CN 101451217A CN A2007101805972 A CNA2007101805972 A CN A2007101805972A CN 200710180597 A CN200710180597 A CN 200710180597A CN 101451217 A CN101451217 A CN 101451217A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 62
- 239000010959 steel Substances 0.000 title claims abstract description 62
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000005096 rolling process Methods 0.000 claims abstract description 27
- 238000001816 cooling Methods 0.000 claims abstract description 16
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910001566 austenite Inorganic materials 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 8
- 238000001953 recrystallisation Methods 0.000 claims description 6
- 238000002791 soaking Methods 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 3
- 230000007704 transition Effects 0.000 claims description 3
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 abstract description 8
- 229910052799 carbon Inorganic materials 0.000 abstract description 7
- 238000003466 welding Methods 0.000 abstract description 7
- 238000013461 design Methods 0.000 abstract description 6
- 230000000694 effects Effects 0.000 abstract description 5
- 239000003345 natural gas Substances 0.000 abstract description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 description 9
- 238000005728 strengthening Methods 0.000 description 7
- 239000010936 titanium Substances 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 230000008878 coupling Effects 0.000 description 2
- 238000010168 coupling process Methods 0.000 description 2
- 238000005859 coupling reaction Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- -1 P≤0.014% Inorganic materials 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000012797 qualification Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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Abstract
The invention relates to steel for pipeline use and a production method thereof. The steel for pipeline use comprises the following chemical components by weight percentage: less than or equal to 0.06 percent of C, less than or equal to 0.23 percent of Si, 1.50 to 1.60 percent of Mn, less than or equal to 0.014 percent of P, less than or equal to 0.008 percent of S, 0.15 to 0.25 percent of Ni, 0.18 to 0.25 percent of MO, 0.025 to 0.035 percent of V, 0.040 to 0.050 percent of Nb, 0.15 to 0.25 percent of Ti, 0.020 to 0.060 percent of Al, and the balance being Fe and unavoidable impurities. The steel is the Mn-Ni-Nb-V series ferrite plus pearlitic steel with the greatly improved strength grade through the low carbon chemical component design, the microalloying and controlled rolling, and the comprehensive use of the stiffening effects of grain refinement and the precipitated phase and dislocation substructure of the microalloying elements. Through the low carbon equivalent component design and the production method of controlled rolling and cooling, the high strength steel for pipeline use is produced and is applied to natural gas transportation pipelines. The steel has good welding performance and lamellar tearing resistance and can meet the requirements for the key strained locations of the site. The steel has the simple manufacturing process and realizes volume production.
Description
Technical field
The present invention relates to a kind of pipeline steel, relate in particular to a kind of X70 pipeline steel, simultaneously, also relate to a kind of production method of this steel plate.
Background technology
Oil and gas is the important component part of national economy, it is the basic substance of social development, sustainable development along with World Oil Industry, pipe-line transportation oil gas is a kind of economic security and continual extensive mode of transport, like this only to require pipe line steel to have high strength, weldability, and requirement should have good toughness, fatigue crack-resistant and corrosion resistance nature, simultaneously tube quality is also had very strict requirement, to smelt, rolling, tubulation and pipe-line construction Technology and equipment capability all be huge test.The explored oil of China, gas reserves often are distributed in rugged, remote area, and these places are cold or the unsettled place of geology often, has so just brought great challenge to pipeline with material, especially " on this engineering of West-east Gas.Carry the purity of the pipeline steel to steel of high pressure, high-density medium to require very high, the addition of alloying element is restricted, therefore research has high-intensity high-tenacity, and good weldability and corrosion proof imperative with the pipe line steel of reasonably process system production by suitable composition is arranged.
Summary of the invention
The object of the present invention is to provide a kind of pipeline steel with good welds and solidity to corrosion and high strength, high tenacity coupling.
Simultaneously, the present invention also aims to provide a kind of production method of this pipeline steel, so that welding property is good, to satisfy the requirement of different site construction technology conditions.
To achieve these goals, technical scheme of the present invention has adopted a kind of pipeline steel, is consisted of by the chemical ingredients of following weight percentage: C≤0.06%, Si≤0.23%, Mn 1.50%-1.60%, P≤0.014%, S≤0.008%, Ni 0.15-0.25%, MO 0.18-0.25%, V 0.025-0.035%, Nb 0.040-0.050%, Ti 0.15-0.25%, Al 0.020-0.060%, all the other are Fe and unavoidable impurities.
Preferred, specifically the chemical ingredients by following weight percentage consists of: C 0.03-0.06%, Si≤0.23%, Mn 1.50%-1.56%, P≤0.014%, S≤0.008%, Ni 0.15-0.19%, MO 0.18-0.22%, V 0.025-0.027%, Nb 0.040-0.047%, Ti 0.15-0.21%, Al 0.020-0.060%, all the other are Fe and unavoidable impurities.
Simultaneously, technical scheme of the present invention has also adopted a kind of production method of pipeline steel, may further comprise the steps:
(1) heating process: the steel billet that will contain above Chemical Composition realizes that temperature is sent, Wen Qing, temperature dress, adopts low speed to burn steel, and temperature is below 1000 ℃, heat-up rate≤120 ℃/h, 1240 ℃ of maximum heating temperatures, soaking time 〉=3.5 hour, soaking zone time inside furnace 〉=60min;
(2) rolling technology: adopt II type controlled rolling process, the fs is the austenite recrystallization stage, and Heating temperature is 950-1150 ℃; Subordinate phase is the non-recrystallize stage of austenite, II stage start rolling temperature should be controlled at≤and 950 ℃, when finishing temperature was 780 ℃-810 ℃, austenite was 500-540 ℃ to the transition temperature of acicular ferrite;
(3) water-cooling process: the steel plate after rolling carries out online cooling, returns 500-540 ℃ of red final cooling temperatures.
Most of reductions in pass of fs are 8～25% in the described step (2), accumulative total draft 〉=70%.
The steel thickness that dries in the air in the described step (2) in the subordinate phase is 3-4 times of finished product thickness.
The subordinate phase draft should be tried one's best greatly in the described step (2), accumulative total draft 〉=50%.
The red temperature of returning in the described step (3) is controlled at 520 ℃, and speed of cooling is 10-20 ℃/s.
The chemical composition design of steel plate of the present invention adopts low-carbon (LC), by microalloying and controlled rolling, the comprehensive utilization grain refining, the precipitated phase of micro alloying element and the strengthening effect of dislocation substructure, it is ferrite+perlitic steel that intensity rank improves a lot of Mn-Ni-Nb-V.The present invention is by low-carbon-equivalent composition Design and controlled rolling and controlled cooling production method, produce and meet the requirement of pipeline with high-strength steel, be applied to natural-gas transfer pipeline, have good welding property and anti-lamellar tearing performance, satisfy the requirement at on-the-spot crucial stressed place, accomplish to manufacture operation simple, can realize producing in batches.The strengthening mechanism of using is build up, refined crystalline strengthening, precipitation strength and solution strengthening.Wherein main and other elements formation carbide of C play build up and precipitation strength, to increase armor plate strength; Mn mainly plays solution strengthening and reduces transformation temperature, to improve the effect of armor plate strength; For effectively realizing the steel plate refined crystalline strengthening by controlled rolling process, must add the Nb element, to reach the raising steel plate recrystallization temperature, heating solid solution Nb stops austenite crystal to be grown up, and high temperature is separated out C, the Nization thing of Nb during cooling; After the controlled rolling of II type, the C of V, Nization thing are separated out, and have improved the intensity of steel plate greatly; It is to increase austenitic condensate depression that Ni mainly acts on, thereby thinning microstructure is obtained strengthening effect.Can also increase the atmospheric corrosion resistance ability of steel in addition, improve low-temperature impact toughness and reduce Cold Brittleness Transition Temperature; Impurity element P, S equal size roll off the production line and do not limit, and reduce as far as possible under the processing unit ability, and steel is pure to reach, the uniform purpose of mechanical property; The main effect of Al is crystal grain thinning, fixed nitrogen, reduces gas content; Ti, in controlled rolling low-carbon (LC) pipe line steel, adding 0.021% titanium can crystal grain thinning, improve the yield strength and the toughness of steel, because titanium at high temperature can combine with N, form the TiN particle, so the crystal grain control of the adding of titanium heat affected zone when helping welding, highly beneficial to the toughness of improving welded heat affecting zone.Condition of delivery of the present invention is the abundant grain refining of controlled rolling, has obtained acicular ferrite structure in the speed of cooling scope of broad, and its performance index are significantly better than other controlled rolling steel.Owing to adopt II type controlled rolling process, solve the mill milling insufficient pressure and the thick inequality of crystal grain, the impelling strength that cause lower phenomenon, and increased the thickness specification that can produce steel plate, be fit to the low rolling pressure milling train production controlled rolling type high-strength steel of other steel mill.
The experiment proved that: steel plate of the present invention has low-carbon-equivalent, higher low-temperature flexibility value and good welding property and corrosion resisting property, also satisfy the design requirements of pipeline steel fully, the present invention adopts cooling controlling and rolling controlling process production, do not carry out quenching heat treatment, simplified production process, reduced the allocation and transportation of the middle operation of steel plate and shifted, shortened the production cycle, be fit to produce in enormous quantities.
The present invention has the following advantages: it is purer that (1) has a steel, P≤0.014%, S≤0.008%; (2) higher intensity and toughness are arranged; (4)-20 ℃ low-temperature flexibility is good; (5) good weldability and solidity to corrosion are arranged.
Test-results shows: the steel plate that adopts method of the present invention to produce has that purity is higher, composition evenly, the characteristics of interior solid, the metallurgical level of steel is higher, mechanical property satisfies the standard-required of pipeline of transferring natural gas from the west to the east fully.Composition is pressed the design of low-carbon-equivalent steel, has good obdurability coupling.Ceq in kind≤0.40%, Pcm≤0.18%, the welding qualification test shows that steel plate has lower welding crack sensibility index, is suitable for pipeline of transferring natural gas from the west to the east.
Shown in the test-results table 1:
Table 1
Embodiment
The actual constituent of pipeline steel of the present invention (by weight percentage) is: C 0.05%, Si 0.22%, Mn 1.52%, P 0.012%, S 0.004%, Ni 0.20%, Al 0.020%, Nb 0.045%, V0.028%, Mo 0.20% and Ti 0.018%, Ceq is 0.38%, and all the other are Fe and unavoidable impurities.Its mechanical property: yield strength 565MPa, tensile strength: 635MPa, yield tensile ratio=0.89, δ 5=36% ,-20 ℃ of ballistic work AKV (vertically) 383,394,367J, fracture shear area: 100,100,100%.
Its production method may further comprise the steps:
(1) heating process: the steel billet that will contain above-mentioned Chemical Composition realizes that temperature is sent, Wen Qing, temperature dress, tiny for guaranteeing the abundant solid solution of alloying element, r crystal grain, adopt low speed to burn steel, heat-up rate below 1000 ℃≤120 ℃/h, 1240 ℃ of maximum heating temperatures, soaking time is 3.5 hours, and the soaking zone time inside furnace is 80min;
(2) rolling technology: adopt II type controlled rolling process, the fs is the austenite recrystallization stage, and Heating temperature is 1100 ℃, most of reductions in pass of this stage are 8～25%, accumulative total draft 〉=70% makes austenite generation perfect recrystallization, with refine austenite crystal grain; Subordinate phase is the non-recrystallize stage of austenite, start rolling temperature is for being 920 ℃, II stage start rolling temperature should be controlled at 950 ℃, the steel thickness that dries in the air is 3.5 times of finished product thickness, when finishing temperature is 780 ℃, in this stage, austenite crystal is elongated, form high-density mechanical twin and deformed belt in the austenite of non-recrystallization in elongation, simultaneously microalloy carbon, nitride are separated out because of deformation induced, thereby have increased ferritic nucleation site, refinement ferrite crystal grain, this stage draft should be tried one's best greatly, accumulative total draft 〉=50%;
(3) water-cooling process: the steel plate after rolling carries out online cooling at the ACC quickly cooling device, returns red temperature and is controlled at 520 ℃, and 15 ℃/S of speed of cooling can obtain optimum performance numerical value.
It should be noted last that: above embodiment is the unrestricted technical scheme of the present invention in order to explanation only, although the present invention is had been described in detail with reference to the foregoing description, those of ordinary skill in the art is to be understood that: still can make amendment or be equal to replacement the present invention, and not breaking away from any modification or partial replacement of the spirit and scope of the present invention, it all should be encompassed in the middle of the claim scope of the present invention.
Claims (7)
1, a kind of pipeline steel is characterized in that: the chemical ingredients by following weight percentage consists of: C≤0.06%, Si≤0.23%, Mn 1.50%-1.60%, P≤0.014%, S≤0.008%, Ni 0.15-0.25%, MO 0.18-0.25%, V 0.025-0.035%, Nb 0.040-0.050%, Ti 0.15-0.25%, Al 0.020-0.060%, all the other are Fe and unavoidable impurities.
2, pipeline steel according to claim 1 is characterized in that: specifically the chemical ingredients by following weight percentage consists of: C 0.03-0.06%, Si≤0.23%, Mn 1.50%-1.56%, P≤0.014%, S≤0.008%, Ni 0.15-0.19%, MO 0.18-0.22%, V 0.025-0.027%, Nb 0.040-0.047%, Ti 0.15-0.21%, Al 0.020-0.060%, all the other are Fe and unavoidable impurities.
3, a kind of production method of pipeline steel as claimed in claim 1 is characterized in that: may further comprise the steps:
(1) heating: the steel billet that will contain above Chemical Composition realizes that temperature is sent, Wen Qing, temperature dress, adopts low speed to burn steel, and temperature is below 1000 ℃, heat-up rate≤120 ℃/h, 1240 ℃ of maximum heating temperatures, soaking time 〉=3.5 hour, soaking zone time inside furnace 〉=60min;
(2) rolling: adopt II type controlled rolling process, the fs is the austenite recrystallization stage, and Heating temperature is 950-1150 ℃; Subordinate phase is the non-recrystallize stage of austenite, II stage start rolling temperature should be controlled at≤and 950 ℃, when finishing temperature was 780 ℃-810 ℃, austenite was 500-540 ℃ to the transition temperature of acicular ferrite;
(3) water-cooled: the steel plate after rolling carries out online cooling, returns 500-540 ℃ of red final cooling temperatures.
4, the production method of pipeline steel according to claim 3 is characterized in that: most of reductions in pass of fs are 8～25% in the described step (2), accumulative total draft 〉=70%.
5, the production method of pipeline steel according to claim 3 is characterized in that: the steel thickness that dries in the air in the described step (2) in the subordinate phase is 3-4 times of finished product thickness.
6, the production method of pipeline steel according to claim 3 is characterized in that: the subordinate phase draft should be tried one's best greatly in the described step (2), accumulative total draft 〉=50%.
7, the production method of pipeline steel according to claim 3 is characterized in that: the red temperature of returning in the described step (3) is controlled at 520 ℃, and speed of cooling is 10-20 ℃/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2007101805972A CN101451217A (en) | 2007-11-30 | 2007-11-30 | Steel for pipeline and method for producing the same |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2007101805972A CN101451217A (en) | 2007-11-30 | 2007-11-30 | Steel for pipeline and method for producing the same |
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| Publication Number | Publication Date |
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| CN101451217A true CN101451217A (en) | 2009-06-10 |
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| CNA2007101805972A Pending CN101451217A (en) | 2007-11-30 | 2007-11-30 | Steel for pipeline and method for producing the same |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102119236A (en) * | 2009-10-28 | 2011-07-06 | 新日本制铁株式会社 | Steel plate for line pipes with excellent strength and ductility and process for production of same |
| CN102400039A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Steel with good low-temperature toughness for slurry conveying pipeline and manufacturing method thereof |
| CN102400053A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Steel plate with yield strength of 460MPa for building structure and manufacturing method thereof |
| CN102953003A (en) * | 2012-11-19 | 2013-03-06 | 宝山钢铁股份有限公司 | Pipeline steel and manufacturing method thereof |
| CN103572023A (en) * | 2013-10-24 | 2014-02-12 | 南京钢铁股份有限公司 | Method for producing ultra-fine grains on surface layer of thick/ultra-thick low-alloy steel plate |
| CN106676240A (en) * | 2016-12-22 | 2017-05-17 | 钢铁研究总院 | Manufacturing method of low alloy steel thick plate with surface-layer ultra-fine grain ferrite |
| CN107385326A (en) * | 2017-06-27 | 2017-11-24 | 南京钢铁股份有限公司 | A kind of production technology of the generous Pipeline Steel Plate of ultra-fine grain |
| CN110004358A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of low big thickness of Pcm value easily welds marine worker steel plate and its production method |
-
2007
- 2007-11-30 CN CNA2007101805972A patent/CN101451217A/en active Pending
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102119236B (en) * | 2009-10-28 | 2013-07-10 | 新日铁住金株式会社 | Steel plate for line pipes with excellent strength and ductility and process for production of same |
| US8641836B2 (en) | 2009-10-28 | 2014-02-04 | Nippon Steel & Sumitomo Metal Corporation | Steel plate for line pipe excellent in strength and ductility and method of production of same |
| CN102119236A (en) * | 2009-10-28 | 2011-07-06 | 新日本制铁株式会社 | Steel plate for line pipes with excellent strength and ductility and process for production of same |
| CN102400053B (en) * | 2010-09-07 | 2014-03-12 | 鞍钢股份有限公司 | Steel plate with yield strength of 460MPa for building structure and manufacturing method thereof |
| CN102400039A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Steel with good low-temperature toughness for slurry conveying pipeline and manufacturing method thereof |
| CN102400053A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Steel plate with yield strength of 460MPa for building structure and manufacturing method thereof |
| CN102953003A (en) * | 2012-11-19 | 2013-03-06 | 宝山钢铁股份有限公司 | Pipeline steel and manufacturing method thereof |
| CN103572023A (en) * | 2013-10-24 | 2014-02-12 | 南京钢铁股份有限公司 | Method for producing ultra-fine grains on surface layer of thick/ultra-thick low-alloy steel plate |
| CN103572023B (en) * | 2013-10-24 | 2015-05-27 | 南京钢铁股份有限公司 | Method for producing ultra-fine grains on surface layer of thick/ultra-thick low-alloy steel plate |
| CN106676240A (en) * | 2016-12-22 | 2017-05-17 | 钢铁研究总院 | Manufacturing method of low alloy steel thick plate with surface-layer ultra-fine grain ferrite |
| CN107385326A (en) * | 2017-06-27 | 2017-11-24 | 南京钢铁股份有限公司 | A kind of production technology of the generous Pipeline Steel Plate of ultra-fine grain |
| CN107385326B (en) * | 2017-06-27 | 2019-06-04 | 南京钢铁股份有限公司 | A kind of production technology of the generous Pipeline Steel Plate of ultra-fine grain |
| CN110004358A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of low big thickness of Pcm value easily welds marine worker steel plate and its production method |
| CN110004358B (en) * | 2019-03-29 | 2021-05-25 | 山东钢铁集团日照有限公司 | Marine steel plate with low Pcm value, large thickness and easy welding and production method thereof |
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Open date: 20090610 |