CN102828125B - Strain design based pipe line steel X70 and its manufacturing method - Google Patents
Strain design based pipe line steel X70 and its manufacturing method Download PDFInfo
- Publication number
- CN102828125B CN102828125B CN201110160120.4A CN201110160120A CN102828125B CN 102828125 B CN102828125 B CN 102828125B CN 201110160120 A CN201110160120 A CN 201110160120A CN 102828125 B CN102828125 B CN 102828125B
- Authority
- CN
- China
- Prior art keywords
- temperature
- steel
- cooling
- rolling
- controlled
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses strain design based pipe line steel X70 and its manufacturing method. the steel comprises the following ingredients of: by weight, 0.06-0.10% of C, 0.1-0.6% of Si, 1.0-2.5% of Mn, P being less than or equal to 0.015%, S being less than or equal to 0.003%, Cr being less than 0.1%, 0.05-0.35% of Mo, 0.01-0.15% of Nb, 0.005-0.03% of Ti, 0.01-0.06% of Al, one or two components selected from 0-0.5% of Cu and 0-0.5% of Ni, and the balance Fe and unavoidable microscale impurities. The manufacturing method is characterized in that slab heating temperature is 1050-1280 DEG C by a controlled rolling and controlled cooling method; the temperature for controlled rolling in a recrystallization zone is controlled within the range of 900-1250 DEG C; the temperature for controlled rolling in a non-recrystallization zone is controlled within the range of 700-950 DEG C; initial cooling temperature is 650-800 DEG C; finish cooling temperature is 100-500 DEG C; and cooling rate is 5-35 DEG C/s. According to the invention, elements of V, B and the like are not added, and the total amount of Mo, Cu, Cr and Ni is low. In addition, subsequent heat treatment is not required, the process is simple and requires low cost, and production efficiency is high.
Description
Technical field
The present invention has designed a kind of pipeline steel and manufacture method thereof, particularly a kind of X70 pipeline steel and manufacture method thereof based on stress design.Pipe line steel prepared by application the present invention can be applied to the line pipe of the employing X70 grade of steels such as polar region, tundra, seismic zone and deep-sea, and various pressurized vessel and welding steel for engineering machinery.
Background technology
In recent years, the variation of energy structure and the growth to energy demand, greatly promoted exploration and the exploitation of new hydrocarbon resources.Large reserves oil field and the natural-gas field found are at present distributed in the special geologic condition regions such as polar region, tundra, seismic zone and deep-sea more.In the extensive motion of these regional stratums or seabed ocean current, pipe line steel not only will bear higher interior pressure, also must there is quite high deformability and strain hardening ability, to bear the axial crushing deformation and the flexural deformation that cause due to geological fault relative movement, seismic wave propagation, liquefaction of soil, bathycurrent simultaneously.Obviously, via such regional pipeline failure, no longer by stress control, and by strain control, simple high-intensity high-tenacity can not be guaranteed the safety of pipeline, and pipe line steel also should have good Chinese People's Anti-Japanese Military and Political College adaptability to changes.Based on this, in steel for pipe selection design, should use the method for design based on strain to replace the method for design based on stress.
Based on the pipeline steel of stress design, except lateral performance (as intensity, yield tensile ratio, unit elongation, ballistic work, the shear area etc. of dropping hammer) meets based on stress design required standard, also Chinese People's Anti-Japanese Military and Political College's adaptability to changes of its longitudinal performance is made to strict regulation.The canonical parameter that characterizes Chinese People's Anti-Japanese Military and Political College's adaptability to changes has: high uniform elongation (UEL >=10%), low yield strength ratio (Y/T≤0.85) and the stress-strain(ed) curve without yield point elongation (cupola type).
Pipeline steel based on stress design is that pipe line steel develops one of challenging field of tool.At present, the pipe line steel of domestic employing TMCP explained hereafter high-intensity high-tenacity is mature on the whole, and particularly " enforcement of a series of key state projects such as West-east Gas, X70, X80 pipe line steel are applied on a large scale.But, current X70, the X80 level pipeline pipeline steel capital is typical perlite or acicular ferrite structure less, plate property corresponding to such organization type has good intensity and toughness coupling, but its plasticity deficiency, homogeneous deformation unit elongation UEL is not more than 10%, yield tensile ratio is mostly more than 0.85, and what have even reaches 0.92.Adopt the pipe line steel of traditional TMCP explained hereafter, can not meet the selection standard based on stress design method.
Current, the research of the pipe line steel based on stress design all has report both at home and abroad, but there are the following problems: as patent US5545270A, US5531842, US5755895A and CN101456034A etc. provide composition and the manufacture method of X80 and above rank two-phase pipe line steel thereof, X70 level pipeline pipeline steel is not related to, and add a large amount of high price metallic element Mo, Ni, Cr etc., be not suitable for the production of high performance-price ratio pipe line steel.Particularly patent US5545270A, US5531842 and US5755895A, proposes to carry out three stage rolling, has increased an intermediate blank and has treated temperature, has reduced production efficiency; Last rolling need to be carried out between two-phase region, and because rolling temperature is low, rolling drag is high requires harshness to milling train.Paper Development of a high-deformability linepipe with resistance to strain-aged hardening by HOP (heat-treatment on-line process), JFE Technical Report No.12 (Oct.2008), relate to composition, the process and performance of X70 large-strain pipeline steel, but the acquisition of its Chinese People's Anti-Japanese Military and Political College's strain characteristics, has benefited from follow-up HOP technique.
Summary of the invention
In order to overcome the shortcoming of above-mentioned prior art, technical problem to be solved by this invention is to provide a kind of adaptability to changes X70 of Chinese People's Anti-Japanese Military and Political College level pipeline pipeline steel of carrying geologic condition severe area hydrocarbon resources and can economical and efficient producing that meets, special design a kind of pipeline steel X70 based on stress design and preparation method thereof.
The Composition Design scheme of pipe line steel of the present invention, compared with traditional X-ray 70, adopts the alloying elements such as higher carbon content, a small amount of selective interpolation Cu, Ni, Mo, Cr, and adds a small amount of microalloy element such as Nb, Ti.Be organized as the heterogeneous structure of polygonal ferrite and bainite.Polygonal ferrite uniform elongation is high, bainite intensity is good, suitable two-phase volume fraction coupling can obtain simultaneously highly evenly extend, suitable intensity, good toughness, high strain-hardening index and low yield tensile ratio.
In the present invention, the content range of each composition by weight percentage: C0.06%-0.10%, Si0.1%-0.6%, Mn1.0%-2.5%, P≤0.015%, S≤0.003%, Cr < 0.1%, Mo0.05%-0.35%, Nb0.01%-0.15%, Ti 0.005%-0.03%, Al0.01%-0.06%; Contain one or both in Cu, Ni, Cu 0%-0.5%, Ni 0%-0.5% simultaneously; Surplus is Fe and inevitably impurity of trace.
As follows with the effect of the chief component composition of pipe line steel X70 based on stress design in the present invention:
C: most economical, the most basic strengthening element in steel, by solution strengthening and precipitation strength, the intensity that improves steel is had to obvious effect, have negative impact but improve ductility, toughness and the weldability of C content to steel, for this reason, the present invention is set as 0.10% by C upper content limit.Modern age, the evolution of pipe line steel was the process that constantly reduces C content.Reduce the toughness that C content contributes to improve steel on the one hand, can improve on the other hand the welding property of steel.In the time that C content is too low, can not give full play to the precipitation strength effect of the elements such as Nb, the present invention is 0.06% by C content lower limit set.
Si: adding Si is for deoxidation in steelmaking process and the intensity that improves matrix.If add excessive Si, the toughness of the welded heat affecting zone of mother metal will significantly reduce, and field welding procedure performance also can variation.Therefore, Si content is set as 0.01-0.60% in the present invention.
Mn: improving the intensity of steel by solution strengthening, is to compensate the main and most economical strengthening element that causes loss of strength because of the reduction of C content in pipe line steel.Mn still expands the element of γ phase region, can reduce γ → α transformation temperature of steel, contributes to obtain tiny phase-change product, can improve toughness, the reduction ductile-brittle transition temperature of steel.For the balance between proof strength and low-temperature flexibility, the minimum content of Mn is set as 1.0%.Improve the content of Mn, the hardenability characteristic of steel increases, and after content is increased to a certain degree, can cause the welding property especially toughness of severe exacerbation welded heat affecting zone that declines.In addition, too high Mn content also can increase continuously cast bloom center segregation, and the anisotropy of plate property is increased.Therefore, Mn upper content limit of the present invention is designed to 2.5%.
Nb: be one of topmost element in modern microalloying pipe line steel, fairly obvious to the effect of grain refining.Separate out and hinder the austenitic recovery and recrystallization of deformation by NbC strain inducing in course of hot rolling, in the time of phase transformation, change tiny phase-change product into through controlled rolling and the cooling deformation austenite structure that makes the rolling of non-recrystallization zone of control, so that steel has high strength and high tenacity.The present invention coordinates C content to add the effect of appropriate Nb performance NbC, and the present invention chooses Nb content range 0.01%-0.15%.
Ti: be strong solid N element, the stoichiometric ratio of Ti/N is 3.42, utilizes the Ti of 0.01% left and right just can fix the N about 30ppm in steel, can form the TiN precipitated phase of tiny high-temperature stable in the time of sheet billet continuous casting.Austenite Grain Growth when this tiny TiN particle can effectively suppress slab and reheats, contributes to improve the solid solubility of Nb in austenite, improves the impelling strength of welded heat affecting zone.When the content of Als too low (as lower than 0.005%), Ti can form oxide compound, and in these, raw particle can play the effect of intracrystalline ferrite forming core core, refinement welded heat affecting zone tissue.In order to obtain this effect, at least to add 0.005%Ti.When Ti addition exceedes certain certain value, TiN particle will alligatoring, and the precipitation strength effect of TiC manifests, and causes low-temperature flexibility to worsen.Therefore, the present invention chooses Ti content range 0.005%-0.03%.
The existence of Al:Al, normally as the reductor in steel, also has the effect of thinning microstructure.But when the content of Al exceedes 0.06%, thereby the amount of aluminum oxide nonmetal inclusion increases the cleanliness factor that reduces steel.The too low deoxidation of Al content is insufficient, and the oxidizable element such as Ti will form oxide compound, and therefore the content lower limit set of Al is 0.01%.
Cr, Mo: be to expand γ phase region, while postponing γ → α phase transformation, first separate out ferrite and form, promote the principal element that acicular ferrite forms, play an important role to controlling phase-change organization, under certain cooling conditions and finishing temperature, in Ultra-low carbon pipe line steel, add, just can obtain obvious acicular ferrite and bainite structure, because phase transformation changes to low temperature direction, can make to organize further refinement, structure refinement is conducive to the improvement of low-temperature flexibility simultaneously.In order to obtain the reasonably combined of intensity, plasticity and toughness, the present invention chooses Cr < 0.10%, Mo0.05%-0.35%.
Cu, Ni: can improve by solution strengthening effect the intensity of steel, Cu can also improve the solidity to corrosion of steel simultaneously, and adding of Ni is mainly to improve the red brittleness that Cu easily causes in steel, and useful to low-temperature flexibility.In thick specification pipe line steel, also can compensate the strength degradation that the water-cooled undercapacity that causes because of the increase of thickness causes.The present invention chooses Cu0%-0.50%, Ni0%-0.50%.
P, S: be inevitable impurity element in steel, it is more low better to wish.For the consideration of smelting cost, again can not be unconfined low.Therefore, the present invention is set as 0.015% and 0.003% by P, S upper content limit.Process sulfide is carried out to inclusion morphology control by ultralow S (being less than 30ppm) and Ca, can make pipe line steel there is high impelling strength.
Therefore, for ferrite+bainite, duplex structure has the features such as high uniform elongation, low yield strength ratio, taking material reinforcement theories such as grain refining, phase transformation strengthening, precipitation strength and dislocations strengthenings as basis, adopt low-carbon (LC), super low sulfur, Nb, Ti combined microalloying to thering is the Composition Design of the X70 of duplex structure pipe line steel, controlled Mo, the Cr alloying of tissue and suitably added the Composition Design of Cu, Ni.Hot rolling technology has adopted the thermomechanical treatment technology of controlled rolling and controlled cooling, carries out the organizational controls of the finished product by reasonable component and technique, has high strength, the ferrite+bainite structure of high tenacity, high uniform elongation and low yield strength ratio to obtain.
In order to ensure lower yield tensile ratio and mating compared with high-strong toughness, except selecting duplex structure's design, in Plate Production process, also adopt two-stage control rolling technique, wherein first stage rolling is recrystallization zone rolling, the single pass heavy deformation of these stage at least three passages is not less than 15%, reaches the object of abundant refinement original austenite grains; Subordinate phase rolling is the rolling of non-recrystallization zone, the cumulative deformation in this stage is not less than 60%, complete the task of the inner dislocation desity accumulation of fetrite grain refinement and crystal grain, after steel plate rolls, in laminar cooling process, adopt the temperature range of specifying to coordinate corresponding speed of cooling.
Pipe line steel of the present invention adopts following operational path: reheat → controlled rolling of get the raw materials ready → converter or electrosmelting → external refining → casting → slab → control cooling.
Hot rolling technology is controlled as follows:
(1) slab heating temperature: 1050-1280 DEG C;
(2) temperature controlling range of recrystallization zone controlled rolling: 900-1250 DEG C;
(3) temperature controlling range of non-recrystallization zone controlled rolling: 700-950 DEG C;
(4) begin to cool down temperature: 650-800 DEG C;
(5) stop cooling temperature: 100-500 DEG C
(6) speed of cooling: 5-35 DEG C/s
Concrete steps are:
A), to carrying out soaking processing after the as cast condition blank cleaning in set component span of control, temperature is controlled in the scope of 1050-1280 DEG C;
B) blank after coming out of the stove is carried out to dephosphorize by high pressure water processing, remove the iron scale that blank produces in heat-processed;
C) blank after dephosphorization is carried out to two-stage control rolling immediately, i.e. recrystallization zone rolling and the rolling of non-recrystallization district, accurately controlled rolling temperature and pass deformation and cumulative deformation;
D) steel plate after finish to gauge carries out air cooling and treats that temperature begins to cool down temperature range to water-cooled, and the austenitic transformation of 30%-70% is for first analysing granular ferrite during this time;
E) steel plate after relaxation is carried out to laminar flow cooling, the steel plate air cooling after water-cooled is to room temperature.In Cooling Process, remaining austenitic transformation is bainite structure, finally obtains proeutectoid ferrite+bainite duplex structure.
The steel plate of the proeutectoid ferrite+bainite duplex structure finally obtaining, it is 485-630MPa that its transverse mechanical performance can reach following requirement: yield strength Rt0.5, tensile strength Rm is 570-760MPa, yield tensile ratio Rt0.5/Rm≤0.80,-20 DEG C of ballistic work CVN >=200J ,-20 DEG C of DWTT shear area SA >=85%.Longitudinal mechanical property of steel plate can reach following requirement: homogeneous deformation elongation UEL >=10%, yield strength Rt0.5 >=400MPa, tensile strength Rm >=550MPa, yield tensile ratio Rt0.5/Rm≤0.80, stress-strain(ed) curve is without yield point elongation and Rt1.5/Rt0.5 >=1.15, and wherein Rt1.5 is that total elongation is 1.5% corresponding stress value.
The invention has the advantages that:
(1) adopt low-carbon (LC) to add Mn, selectively add Cu, Ni, Mo, Cr, do not add the economical Composition Design of V, effectively reduced production cost;
(2) method, i.e. recrystallization zone rolling and the rolling of non-recrystallization district of the rolling of employing two-stage control.In deformation process, adopt suitable texturing temperature and deflection, make austenite crystal obtain effective refinement; Intermediate blank air cooling is treated thermophase, and Niobium Carbonitride Second Phase Precipitation is obvious, and austenite grain boundary obtains effectively pin, and crystal grain stability is good, and obvious grain coarsening phenomenon can not occur;
(3) after finish to gauge, steel plate carries out air cooling and treats temperature, and steel plate is reduced to 10-70 DEG C below ferrite Precipitation Temperature Ar3 entering the water layer stream temperature before cooling, and the austenitic transformation that makes 30%-70% in steel plate is the polygonal ferrite that plasticity is good;
(4) steel plate for the treatment of after temperature carries out laminar flow order but, speed of cooling scope control is at 5-35 DEG C/s, final cooling temperature is controlled within the scope of 100-500 DEG C, ensure in Cooling Process, remaining austenitic transformation is bainite structure, the polygonal ferrite of first separating out can obviously not grown up, and finally obtains polygonal ferrite+bainite duplex structure;
(5) the cooled steel plate air cooling of laminar flow is to room temperature, and intensity and plasticity index are good.It is 485-630MPa that the transverse mechanical performance of steel plate can reach following requirement: yield strength Rt0.5, and tensile strength Rm is 570-760MPa, yield tensile ratio Rt0.5/Rm≤0.80 ,-20 DEG C of ballistic work CVN >=200J ,-20 DEG C of DWTT shear area SA >=85%.Longitudinal mechanical property of steel plate can reach following requirement: homogeneous deformation elongation UEL >=10%, yield strength Rt0.5 >=400MPa, tensile strength Rm >=550MPa, yield tensile ratio Rt0.5/Rm≤0.80, stress-strain(ed) curve is without yield point elongation and Rt1.5/Rt0.5 >=1.15.
By application this patent, the X70 level pipeline pipeline steel of production that can economical and efficient based on stress design.The advantage of this patent is selectively to add the alloying elements such as Cu, Cr, Ni, Mo, and each alloying element total amount has reduction in various degree, and does not need subsequent heat treatment, and therefore manufacturing process is simple, cost is lower.The X70 pipe line steel of application the present invention production, except meeting the requirement of strength of traditional X-ray 70, also has low yield strength ratio and high feature of evenly extending, and is applied to X70 line pipe and will increases substantially the security that pipeline is runed.
Embodiment
Below in conjunction with embodiment, the present invention is further described:
Chemical composition, processing parameter and the results of property of embodiment 1-12, comparative example 13-16 is as shown in table 1-4.
1. chemical composition
The chemical composition (wt%) of embodiment 1-12 and comparative example 13-16 is as table 1.
Table 1 chemical composition (wt%)
| C | Si | Mn | P | S | Ti | Nb | Cu | Ni | Cr | Mo | Al | |
| 1 | 0.06 | 0.33 | 1.68 | 0.01 | 0.003 | 0.017 | 0.03 | 0.24 | 0.23 | 0.09 | 0.05 | 0.04 |
| 2 | 0.06 | 0.26 | 1.64 | 0.01 | 0.003 | 0.012 | 0.04 | 0.15 | 0.15 | 0.09 | 0.09 | 0.03 |
| 3 | 0.07 | 0.42 | 1.55 | 0.01 | 0.003 | 0.015 | 0.03 | 0 | 0.45 | 0.05 | 0.05 | 0.03 |
| 4 | 0.07 | 0.35 | 1.52 | 0.01 | 0.003 | 0.015 | 0.04 | 0.45 | 0 | 0.09 | 0.05 | 0.03 |
| 5 | 0.10 | 0.25 | 1.72 | 0.01 | 0.003 | 0.015 | 0.03 | 0.20 | 0.20 | 0.05 | 0.05 | 0.03 |
| 6 | 0.09 | 0.30 | 1.58 | 0.01 | 0.003 | 0.015 | 0.04 | 0.20 | 0.20 | 0 | 0.15 | 0.03 |
| 7 | 0.06 | 0.32 | 1.27 | 0.01 | 0.003 | 0.015 | 0.03 | 0.22 | 0.18 | 0.05 | 0.05 | 0.03 |
| 8 | 0.06 | 0.30 | 1.85 | 0.01 | 0.003 | 0.015 | 0.04 | 0.22 | 0.20 | 0 | 0.15 | 0.03 |
| 9 | 0.07 | 0.30 | 1.50 | 0.01 | 0.003 | 0.015 | 0.03 | 0 | 0.20 | 0.09 | 0.10 | 0.03 |
| 10 | 0.07 | 0.25 | 1.65 | 0.01 | 0.003 | 0.015 | 0.05 | 0.15 | 0 | 0.09 | 0.10 | 0.03 |
| 11 | 0.07 | 0.30 | 1.50 | 0.01 | 0.003 | 0.015 | 0.03 | 0.15 | 0.20 | 0.09 | 0.10 | 0.03 |
| 12 | 0.07 | 0.25 | 1.65 | 0.01 | 0.003 | 0.015 | 0.05 | 0.15 | 0.15 | 0.09 | 0.10 | 0.03 |
| 13 | 0.02 | 0.25 | 1.65 | 0.01 | 0.003 | 0.015 | 0.05 | 0.15 | 0 | 0.60 | 0.10 | 0.03 |
| 14 | 0.05 | 0.30 | 1.50 | 0.01 | 0.003 | 0.015 | 0.03 | 0.15 | 0.20 | 0.10 | 0.10 | 0.03 |
| 15 | 0.06 | 0.25 | 1.65 | 0.01 | 0.003 | 0.015 | 0.05 | 0.15 | 0.15 | 0 | 0.15 | 0.03 |
| 16 | 0.11 | 0.25 | 1.65 | 0.01 | 0.003 | 0.015 | 0.05 | 0.15 | 0.15 | 0 | 0.55 | 0.03 |
2. hot rolling technology
Operational path is as follows: reheat → controlled rolling of get the raw materials ready → converter or electrosmelting → external refining → casting → slab → control cooling.
The processing parameter of embodiment 1-12, comparative example 13-16 is in table 2.
Table 2 processing parameter
3. results of property
Carry out respectively mechanics, Charpy impact, DWTT experiment, the horizontal plate property test-results of embodiment 1-12, comparative example 13-16 is as shown in table 3, and longitudinally performance is as shown in table 4.
Table 3 transverse mechanical results of property
| Yield strength MPa | Tensile strength MPa | Yield tensile ratio | Unit elongation A50% | Ballistic work J@-20 DEG C | SA％-20℃DWTT | |
| 1 | 570 | 760 | 0.75 | 35.9 | 331 | 90 |
| 2 | 531 | 708 | 0.75 | 40.9 | 336 | 90 |
| 3 | 485 | 703 | 0.69 | 39.3 | 348 | 90 |
| 4 | 496 | 689 | 0.72 | 41.5 | 318 | 90 |
| 5 | 490 | 650 | 0.75 | 39.3 | 340 | 90 |
| 6 | 595 | 744 | 0.80 | 41.8 | 292 | 90 |
| 7 | 509 | 679 | 0.75 | 40.2 | 296 | 90 |
| 8 | 491 | 691 | 0.71 | 41.0 | 337 | 90 |
| 9 | 495 | 685 | 0.72 | 38.6 | 277 | 90 |
| 10 | 555 | 730 | 0.76 | 41.9 | 287 | 90 |
| 11 | 610 | 760 | 0.8 | 42.0 | 266 | 90 |
| 12 | 573 | 735 | 0.78 | 35.3 | 345 | 90 |
| 13 | 435 | 600 | 0.73 | 40.1 | 333 | 90 |
| 14 | 599 | 722 | 0.83 | 38.7 | 317 | 90 |
| 15 | 588 | 683 | 0.86 | 39.4 | 264 | 90 |
| 16 | 589 | 720 | 0.82 | 39.8 | 291 | 90 |
Table 4 is mechanics results of property longitudinally
Claims (1)
1. the manufacture method of the pipeline steel X70 based on stress design, it is characterized in that, the component content scope of described steel is by weight percentage: C0.06%-0.10%, Si0.1%-0.6%, Mn1.0%-2.5%, P≤0.015%, S≤0.003%, Cr<0.1%, Mo0.05%-0.35%, Nb0.01%-0.15%, Ti0.005%-0.03%, Al0.01%-0.06%, contain one or both in Cu, Ni simultaneously, Cu0.15%-0.20%, Ni0%-0.5%, surplus is Fe and inevitably impurity of trace; The manufacturing process route of described steel is get the raw materials ready → converter or the reheat → controlled rolling of electrosmelting → external refining → casting → slab → control cooling, wherein, it is 1050-1280 DEG C that slab reheats temperature, the temperature controlling range of recrystallization zone controlled rolling is 900-950 DEG C, the temperature controlling range of non-recrystallization zone controlled rolling is 700-950 DEG C, beginning to cool down temperature is 650-800 DEG C, and termination cooling temperature is 100-500 DEG C, and speed of cooling is 5-35 DEG C/s; Blank after heating is carried out carrying out immediately two-stage control rolling after dephosphorize by high pressure water, and the single pass heavy deformation of first stage at least three passages is not less than 15%, and the cumulative deformation of subordinate phase is not less than 60%; Steel plate after finish to gauge is controlled to cold relaxation to water-cooled and start temperature, make the austenitic transformation of 30%-70% for first analysing granular ferrite, in Cooling Process, making remaining austenitic transformation is bainite, obtains proeutectoid ferrite+bainite duplex structure; It is 485-630MPa that its transverse mechanical performance of described steel reaches following requirement: yield strength Rt0.5, and tensile strength Rm is 570-760MPa, yield tensile ratio Rt0.5/Rm≤0.80 ,-20 DEG C of ballistic work CVN >=200J ,-20 DEG C of DWTT shear area SA >=85%; Longitudinally mechanical property reaches following requirement: homogeneous deformation elongation UEL >=10%, yield strength Rt0.5 >=400MPa, tensile strength Rm >=550MPa, yield tensile ratio Rt0.5/Rm≤0.80, stress-strain(ed) curve is without yield point elongation and Rt1.5/Rt0.5 >=1.15, and wherein Rt1.5 is that total elongation is 1.5% corresponding stress value.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110160120.4A CN102828125B (en) | 2011-06-14 | 2011-06-14 | Strain design based pipe line steel X70 and its manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110160120.4A CN102828125B (en) | 2011-06-14 | 2011-06-14 | Strain design based pipe line steel X70 and its manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102828125A CN102828125A (en) | 2012-12-19 |
| CN102828125B true CN102828125B (en) | 2014-09-03 |
Family
ID=47331430
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201110160120.4A Active CN102828125B (en) | 2011-06-14 | 2011-06-14 | Strain design based pipe line steel X70 and its manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102828125B (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103882327B (en) * | 2012-12-21 | 2016-01-20 | 鞍钢股份有限公司 | There is pipeline steel and the manufacture method thereof of excellent strain aging performance |
| CN103215420B (en) * | 2012-12-31 | 2015-02-04 | 西安石油大学 | Obtaining method of large deformation pipe line steel double phase structure |
| CN103320692B (en) * | 2013-06-19 | 2016-07-06 | 宝山钢铁股份有限公司 | Superhigh tenacity, superior weldability HT550 steel plate and manufacture method thereof |
| CN103981462A (en) * | 2014-05-30 | 2014-08-13 | 秦皇岛首秦金属材料有限公司 | Excellent-toughness large-wall-thickness X80 steel for low-temperature stations, and manufacturing method thereof |
| CN106282841A (en) * | 2015-05-27 | 2017-01-04 | 鞍钢股份有限公司 | A kind of deep-sea oil gas feed-line steel X70 and ultra-thick steel plates hot-rolling method thereof |
| CN105921524B (en) * | 2016-05-11 | 2017-08-25 | 天津钢管集团股份有限公司 | Controlled rolling method in seamless pipe course of hot rolling |
| CN109957709B (en) * | 2017-12-14 | 2020-07-17 | 鞍钢股份有限公司 | V-containing large-deformation X70M pipeline steel plate and manufacturing method thereof |
| CN109957710B (en) * | 2017-12-14 | 2020-07-17 | 鞍钢股份有限公司 | V-containing large-deformation X80M pipeline steel plate and manufacturing method thereof |
| CN109182702A (en) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of heterogeneous structure high-toughness ship plate steel EH40 |
| KR102131538B1 (en) * | 2018-11-30 | 2020-07-08 | 주식회사 포스코 | Ultra high strength steel material having excellent cold workability and sulfide stress cracking resistance and method of manufacturing the same |
| CN112143959B (en) * | 2019-06-27 | 2022-01-14 | 宝山钢铁股份有限公司 | Steel plate with low yield ratio, high toughness and excellent weldability and manufacturing method thereof |
| CN110578091B (en) * | 2019-09-27 | 2021-06-22 | 邯郸钢铁集团有限责任公司 | High-toughness limit thickness-diameter ratio submarine pipeline steel strip and production method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101624688A (en) * | 2009-08-14 | 2010-01-13 | 首钢总公司 | X70 station yard steel with excellent toughness and large wall thickness and production method thereof |
| CN101864535A (en) * | 2009-04-15 | 2010-10-20 | 中国科学院金属研究所 | Large deformation resistant pipeline steel and production technology thereof |
| CN101994059A (en) * | 2009-08-10 | 2011-03-30 | 鞍钢股份有限公司 | Method for producing thin-wall X70 pipeline steel coiled plate with low cost |
-
2011
- 2011-06-14 CN CN201110160120.4A patent/CN102828125B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101864535A (en) * | 2009-04-15 | 2010-10-20 | 中国科学院金属研究所 | Large deformation resistant pipeline steel and production technology thereof |
| CN101994059A (en) * | 2009-08-10 | 2011-03-30 | 鞍钢股份有限公司 | Method for producing thin-wall X70 pipeline steel coiled plate with low cost |
| CN101624688A (en) * | 2009-08-14 | 2010-01-13 | 首钢总公司 | X70 station yard steel with excellent toughness and large wall thickness and production method thereof |
Non-Patent Citations (4)
| Title |
|---|
| 冉旭等.工艺制度对X70抗大变形管线钢组织性能的影响.《热加工工艺》.2009,第38卷(第2期),第38-41,15页. |
| 工艺制度对X70抗大变形管线钢组织性能的影响;冉旭等;《热加工工艺》;20090125;第38卷(第2期);第38-41,15页 * |
| 焦多田等.空冷弛豫对 X70级抗大变形管线钢组织性能的影响.《材料热处理学报》.2009,第30卷(第5期),第101-105页. |
| 空冷弛豫对 X70级抗大变形管线钢组织性能的影响;焦多田等;《材料热处理学报》;20091025;第30卷(第5期);第101-105页 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102828125A (en) | 2012-12-19 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102828125B (en) | Strain design based pipe line steel X70 and its manufacturing method | |
| CN102828120B (en) | Strain design based economical pipe line steel and its manufacturing method | |
| CN103834874B (en) | Heavy wall height DWTT performance X65-70 subsea pipeline steel and manufacture method | |
| CN101397626B (en) | High intensity and high-toughness hot-rolled steel sheet and method for producing the same | |
| CN102851587B (en) | Anti-deformation X80-X100 pipeline steel plate | |
| CN103866204B (en) | The large sstrain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature is produced | |
| CN103225047B (en) | The X80 pipeline steel of thickness >=26.5mm and production method thereof | |
| CN101845596A (en) | Wide thick plate for X80 pipe line steel and manufacturing method thereof | |
| CN105463324A (en) | Thick high-toughness pipeline steel and manufacturing method thereof | |
| CN102953018A (en) | High-strength pipeline steel, steel pipe and manufacture method thereof | |
| CN112575158B (en) | High-plasticity thick-specification pipeline steel plate and manufacturing method thereof | |
| CN102071362A (en) | High performance low carbon bainitic steel and production method thereof | |
| CN104250713A (en) | X80-grade large-deformation-resistant pipeline steel plate and manufacturing method thereof | |
| CN101818304B (en) | Ultra-large linear energy input welding high-strength steel and production method thereof | |
| CN104372257A (en) | Low-alloy high-strength middle-thickness plate capable of utilizing self-tempering waste heat to improve toughness and preparation method of low-alloy high-strength middle-thickness plate | |
| CN109023069A (en) | The effective steel plate of NbC reinforced by nanoparticles X80 plasticity and its manufacturing method | |
| CN102400062B (en) | X130 pipe line steel with low yield ratio and ultrahigh strength and manufacturing method of hot rolled flat plate of X130 pipe line steel | |
| CN109957709B (en) | V-containing large-deformation X70M pipeline steel plate and manufacturing method thereof | |
| CN106319388A (en) | 80 kg-level low preheating type high-strength steel plate and manufacturing method thereof | |
| CN109023068A (en) | The effective steel plate of VC reinforced by nanoparticles X90 plasticity and its manufacturing method | |
| CN109136756A (en) | The effective steel plate of NbC reinforced by nanoparticles X90 plasticity and its manufacturing method | |
| CN102337482B (en) | Bainite high strength and toughness steel plate with yield strength of 900 MPa and manufacture method thereof | |
| CN103667909A (en) | Mobile ocean platform steel with yield ratio not greater than 0.65 and production method thereof | |
| CN109957710A (en) | One kind X80M Pipeline Steel Plate of large deformation containing V and its manufacturing method | |
| CN103160756B (en) | Manufacturing method of pipeline steel with high strength and toughness and high deformability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |