CN102154587B - Pipe line steel for high linear energy welding and manufacturing method thereof - Google Patents
Pipe line steel for high linear energy welding and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides pipe line steel for high linear energy welding and a manufacturing method thereof. The pipe line steel for the high linear energy welding comprises the following components in percentage by weight: 0.05 to 0.08 percent of carbon, 0.15 to 0.35 percent of silicon, 1.5 to 1.8 percent of manganese, 0.004 to 0.006 percent of nitrogen, 0.012 to 0.016 percent of titanium, 0.02 to 0.04 percent of aluminum, 0.05 to 0.08 percent of rare earth elements, 0.03 to 0.07 percent of niobium, 0.2 to 0.4 percent of nickel, 0.2 to 0.5 percent of copper, not more than 0.010 percent of phosphorus, not more than 0.005 percent of sulfur, not more than 0.002 percent of oxygen and the balance of Fe and other inevitable impurity elements, wherein the weight ratio of the titanium to the nitrogen is controlled to be between 2 and 4, the weight ratio of the aluminum to the nitrogen is controlled to be between 3 and 10, and the yield strength Rt 0.2 of the pipe line steel for the high linear energy welding is more than 570 MPa. The pipe line steel has a typical needle-like ferritic structure, high comprehensive mechanical properties, high linear energy welding performance and low cost.
Description
Technical field
The present invention relates to the Hi-Stren steel technical field, more particularly, relate to a kind of large-line energy welding pipe line steel and manufacture method thereof.
Background technology
The X80 pipe line steel is a kind of high-strength line-pipe steel, and wherein, X80 divides style number for the high-strength line-pipe steel U.S., and the SMYS of expression pipe line steel is 80000psi (being about 552MPa).
Along with the continuous growth of oil, Sweet natural gas equal energy source consumption, the pipe line steel technical renovation is positive develop rapidly also.The X80 pipe line steel is owing to its high strength, high tenacity have been applied at " transfering natural gas from the west to the east two wires " the gas pipe line engineering of building and the trunk pipeline of Sino-Russian petroleum pipe line engineering.Although existing a lot of big-and-middle-sized steel mills can make the X80 level pipeline pipeline steel at present, though but traditional X80 level pipeline pipeline steel has tough matching preferably, (for example, heat input is more than or equal to 100KJ/cm or more than or equal to 200KJ/cm) uses under the large-line energy welding conditions but all can't satisfy.Usually, the weld heat input at the piping installation scene that existing use X80 pipe line steel welds is all on the low side, generally adopts the welding line of 30KJ/cm can carry out pipeline welding.Pipeline welding has become and has improved pipeline laying efficient, saved one of main bottleneck of cost under the low heat input.
The large heat input welding pipeline steel can significantly improve laying efficient, the saving cost of pipeline, is one of high-intensity high-tenacity pipe line steel main development tendency of future generation.Yet, under the large-line energy welding conditions, the X80 pipe line steel of traditional high-intensity high-tenacity is when welding, there are problems such as the serious alligatoring of crystal grain of coarse-grain heat affected zone and change in organization, this will cause the performance of welded heat affecting zone and the performance of pipe line steel mother metal seriously not to match, and welding joint coarse-grain heat affected zone no longer has many excellent properties of pipe line steel.
At present, in order to improve the performance of X80 level pipeline pipeline steel under the large-line energy welding conditions, significantly reduce this shortcoming to improve welding coarse-grain heat affected zone low-temperature impact toughness, having the scholar to think forms the TiN precipitate and improves welding coarse-grain heat affected zone toughness by add Ti, N element in molten steel, but welding coarse-grain heat affected zone Heating temperature is very high (usually under the large-line energy welding conditions, be higher than 1370 ℃), therefore, TiN can dissolve.
Summary of the invention
Deficiency at the prior art existence, chemical ingredients and/or the condition such as fabrication process parameters of an aspect of of the present present invention by control X80 level pipeline pipeline steel made and can weld the X80 pipe line steel that keeps premium properties under (for example, heat input is more than or equal to 100KJ/cm or more than or equal to 200KJ/cm) condition at large-line energy.This large-line energy welding also can require the steel grade of large-line energy welding to use as other with the X80 pipe line steel, for example, uses with steel as high building structure.Another aspect of the present invention provides a kind of method that the X80 pipe line steel is used in this large-line energy welding of making.
An aspect of of the present present invention provides a kind of large-line energy welding pipe line steel, described large-line energy welding comprises by weight percentage with pipe line steel: 0.05%～0.08% carbon (C), 0.15%～0.35% silicon (Si), 1.5%～1.8% manganese (Mn), 0.004%～0.006% nitrogen (N), 0.012%～0.016% titanium (Ti), 0.02%～0.04% aluminium (Al), 0.05%～0.08% rare earth element (RE), 0.03%～0.07% niobium (Nb), 0.2%～0.4% nickel (Ni), 0.2%～0.5% copper (Cu), be not more than 0.010% phosphorus (P), be not more than 0.005% sulphur (S), be not more than 0.002% oxygen (O) and iron (Fe) and other unavoidable impurities element of surplus, wherein the weight ratio of titanium and nitrogen (Ti/N) control is between 2～4, the weight ratio of aluminium and nitrogen (Al/N) control is between 3～10, and described large-line energy welds the yield strength Rt with pipe line steel
0.2Greater than 570MPa.
In an embodiment of one aspect of the present invention, welding crack sensitivity coefficient Pcm=C+Si/30+ (Mn+Cu)/20+Ni/60≤0.19 of described pipe line steel.
In an embodiment of one aspect of the present invention, described large-line energy welding has acicular ferrite structure with pipe line steel.
In an embodiment of one aspect of the present invention, the welding of described large-line energy with the tensile strength Rm of pipe line steel can greater than 675MPa, elongation A can be greater than 20%, subzero 20 ℃ of horizontal Charpy-V impact powers can be greater than 245J, the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones can be greater than 80J under the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones under the welding analog heat input of 100KJ/cm can be greater than 126J, welding analog heat input at 200KJ/cm.
In an embodiment of one aspect of the present invention, described large-line energy welding can also be used as the non-pipe line steel that requires the large-line energy welding with pipe line steel, for example can be used as high-strength engineering machines and uses with steel.
Another aspect of the present invention provides a kind of method that pipe line steel is used in the large-line energy welding of making, and said method comprising the steps of: smelting has the molten steel that the composition of pipe line steel is used in above-mentioned large-line energy welding with formation; Described molten steel is cast steel billet; Rolling described steel billet, the described rolling recrystallization zone that comprises is rolling rolling with the non-recrystallization district; Cooling is through Rolled Steel, and speed of cooling is 12 ℃/s～25 ℃/s.
In the present invention embodiment on the other hand, described method also can comprise to be controlled the self tempering temperature of steel in 450 ℃～550 ℃ scope.
In the present invention embodiment on the other hand, the rolling start rolling temperature in described recrystallization zone can be controlled in 1150 ℃～1180 ℃ scope, and its finishing temperature may be controlled to greater than 980 ℃; The rolling start rolling temperature in described non-recrystallization district may be controlled to be not more than 880 ℃, and its finishing temperature can be controlled in 780 ℃～820 ℃ scope, and the rolling draft in non-recrystallization district may be controlled to greater than 60%.
In the present invention embodiment on the other hand, the described step that molten steel is cast steel billet can adopt continuous casting process.
Compared with prior art, the present invention has following beneficial effect:
(1) removes expensive chromium (Cr), molybdenum (Mo) element, reduced the Financial cost of pipe line steel;
(2) by titanium nitrogen in the control alloying constituent than (Ti/N) and aluminium nitrogen than (Al/N), make combination products such as having formed suitable Ti, Al, N in the pipe line steel replace titanium nitride (TiN), thereby this combination product can play when high temperature hinder that austenite crystal is grown up and when subcooling as the dual function of the forming core core of acicular ferrite, can also refinement welding coarse-grain heat affected zone (CGHAZ) tissue crystal grain;
(3) add micro-RE element, play crystal grain thinning, improve the rotten effect that is mingled with, thereby improve comprehensive mechanical property and the large-line energy welding property of pipe line steel;
(4) large-line energy welding of the present invention possesses good comprehensive performances with the X80 pipe line steel, is specially: mechanical property Rt
0.2＞570MPa; Rm＞675MPa; Elongation A＞20%;-20 ℃ of horizontal Charpy-V impact power＞245J; Under the welding analog heat input of 100KJ/cm ,-20 ℃ of coarse-grain heat affected zone low-temperature impact work AKv=＞126J; Under the welding analog heat input of 200KJ/cm ,-20 ℃ of coarse-grain heat affected zone low-temperature impact work AKv＞80J.
Embodiment
The invention provides the welding of a kind of large-line energy with X80 pipe line steel and manufacture method thereof, one of problem of its solution is the problem that high tensile pipeline steel that industry makes can not the large-line energy welding.
Large-line energy of the present invention welding with the X80 pipe line steel by remove in the more expensive Cr of price, Mo element, the control steel the titanium weight nitroxide than and aluminium weight nitroxide ratio and add the structure property that measure such as a spot of rare earth RE element improves pipe line steel, its cardinal principle is: (1) removes expensive Cr, the Mo element is to reduce the Financial cost of pipe line steel, add the RE element of trace simultaneously, crystal grain thinning, improvement are gone bad and are mingled with, and improve comprehensive mechanical property and the large-line energy welding property of pipe line steel; (2) in the emphasis control alloying constituent Ti/N, Al/N comprehensively than, make combination products such as formation in the pipe line steel suitable Ti, Al, N replace TiN, in order to when high temperature, play when hindering austenite crystal and growing up effect and subcooling the dual function as the forming core core of acicular ferrite, refinement welding coarse-grain heat affected zone (CGHAZ) tissue crystal grain; (3) reduce the disadvantageous effect to structure property that Cr, Mo bring in order to remedy, rolling (roughing) stage implementation high temperature is depressed the operation with the refinement original austenite grain greatly in the recrystallization zone; Rolling (finish rolling) stage is adopted the rolling principle of low temperature gross distortion in the non-recrystallization district, with the acicular ferrite structure of final formation refinement.
Large-line energy welding according to an aspect of the present invention comprises by weight percentage with the X80 pipe line steel: 0.05%～0.08% carbon, 0.15%～0.35% silicon, 1.5%～1.8% manganese, 0.004%～0.006% nitrogen, 0.012%～0.016% titanium, 0.02%～0.04% aluminium, 0.05%～0.08% rare earth element, 0.03%～0.07% niobium, 0.2%～0.4% nickel, 0.2%～0.5% copper, be not more than 0.010% phosphorus, be not more than 0.005% sulphur, be not more than iron and other unavoidable impurities element of 0.002% oxygen and surplus, wherein the control of the weight ratio of titanium and nitrogen is between 2～4, and the weight ratio of aluminium and nitrogen is controlled between 3～10.The present invention can make complex inclusions such as forming Ti, Al, N in the steel by adopting strict control Ti/N and Al/N, utilizes the complex inclusion stable performance that remains unchanged under 1370 ℃ high temperature to improve welding coarse-grain heat affecting toughness.
In the present invention, the effect played of each main alloy element is as described below.
Carbon is strengthening element most economical, the most basic in the steel, and it is by the intensity that is used for improving steel of solution strengthening and precipitation strength.Yet, have good welding property, good low-temperature impelling strength in order to make steel plate, in the situation of the carbide that guarantees the high-melting-points such as NbC, TiC that formation is enough, the addition of carbon is also unsuitable too high.Therefore, in the present invention, carbon element content is controlled by weight percentage in 0.05%～0.08% scope.
Silicon can improve the critical transition temperature of steel when heating and cooling, increases the effect of thermal hysteresis.Stability and the influence of incubation period that silicon is put following temperature to austenite in critical transitions are little.The Si solid solution in ferrite and austenite, thereby can improve their intensity and hardness.Yet the unfavorable factor of silicon is to impel ferrite grain coarsening in heat-processed.Therefore, in the present invention, silicon content is controlled by weight percentage in 0.15%～0.35% scope.
Manganese is weak carbide forming element, is that compensation reduces the main and most economical strengthening element that causes loss of strength in the pipe line steel because of C content.Mn can spread by the remarkably influenced austenite, is austenitic stable element.Mn also can enlarge the austenite phase region, reduces the γ-α transformation temperature of steel, helps to obtain tiny phase-change product, can improve toughness, the reduction ductile-brittle transition temperature of steel.Simultaneously can also solution strengthening ferrite and the hardening capacity that increases steel.Therefore, in the present invention, manganese element content is controlled by weight percentage in 1.5%～1.8% scope.
Titanium is a kind of important microalloy element, is the element that can play good nitrogen fixation, and it can form the TiN precipitated phase of tiny high-temperature stable when sheet billet continuous casting.Austenite crystal when this tiny TiN particle can hinder the slab reheat is effectively grown up, and crystal grain thinning improves YIELD STRENGTH, also can improve the solid solubility of Nb in austenite, simultaneously the impelling strength of improving welded heat affecting zone is had obvious effect.Therefore, in the present invention, titanium elements content is controlled by weight percentage in 0.012%～0.016% scope.
Aluminium can form the infusible compound that small and dispersed distributes (for example, AlN), the crystal grain that the infusible compound that these small and disperseds distribute to a certain extent can the refinement steel improves the grain coarsening temperature of steel at neutralize other element of steel.Therefore, in the present invention, aluminium element content is controlled by weight percentage in 0.02%～0.04% scope.
Nitrogen is main and strong carbide elements formation precipitates such as Ti, Al in steel, therefore, and must strict Ti/N and the Al/N that controls in the steel.Specifically, Ti/N control between 2～4, is controlled Al/N between 3～10.When Ti/N＞4, thick TiN particle can be formed in the steel, thereby the welding property of steel will be had a strong impact on, when Ti/N＜2, the TiN particle is less in the steel, does not have the corresponding welding property effect of improving.And under the large-line energy welding conditions, because welding heating temperature too high (can reach 1370 ℃ usually), thereby the situation that the TiN particulate fraction dissolves will appear.Therefore, in the present invention, Al/N ratio in the strict control steel, when with Al/N control between 3～10, will form Ti, Al, the compound precipitate of N, the high temperature that this compound precipitate can produce in the large-line energy welding (for example, 1400 ℃) keep stable down, in process of cooling subsequently, the compound precipitate of Ti, Al, N is conducive to acicular ferrite nucleating, improves the low-temperature impact toughness of welded heat affecting zone.Therefore, in the present invention, nitrogen element content is controlled by weight percentage in 0.004%～0.006% scope.
Rare earth element (RE) has cleaning molten steel, makes the effect of inclusion modification in Clean Steel.The solid solubility order of magnitude of Clean Steel middle-weight rare earths can be 10
-5～10
-4, the rare earth of solid solution can influence the Clean Steel quenching structure in the steel, and can crystal grain thinning, thereby has improved the mechanical property of Clean Steel.In addition, rare earth makes the effect of inclusion modification also improve the welding property of steel to a certain extent.Therefore, in the present invention, ree content can be controlled in 0.05%～0.08% the scope by weight percentage.
Niobium can produce significant grain refining and moderate precipitation strength effect.Simultaneously, niobium can also improve austenitic recrystallization temperature.When combining, a large amount of distortion in the course of hot rolling being carried out interpolation niobium element and hot mechanical controlled rolling technology (TMCP), obtain the tiny tissue that has a large amount of deformed belts below recrystallization temperature.Therefore, in the present invention, niobium element content is controlled by weight percentage in 0.03%～0.07% scope.
Nickel can the malleableize matrix, particularly improves the low-temperature flexibility of steel.Along with the increase of nickel content in the steel, ductile-brittle transition temperature significantly reduces, and the low-temperature flexibility of steel is improved significantly.Therefore, among the present invention, nickel element content is controlled by weight percentage in 0.2%～0.4% scope.
Copper can improve solidity to corrosion, the intensity of steel, improves weldability, formability and machinability etc.Face-centered cubic ε-Cu separates out from α-Fe steel are strengthened.Therefore, in the present invention, copper content is controlled by weight percentage in 0.2%～0.5% scope.
As a rule, impurity contents such as the phosphorus in the steel, sulphur, oxygen can cause the deterioration of rigidity energy when too high, and therefore, generally speaking, the phosphorus in the steel, sulphur, oxygen level are more low more good.Specifically, in steel of the present invention, phosphoric is easy to generate segregation, worsen welding property, significantly reduce steel low-temperature impact toughness, improve brittle transition temperature etc.; Element sulphur mainly influences anti-hydrogen embrittlement corrosion (HIC) ability and resisting sulfide stress corrosion (SSC) ability of steel, and in addition, sulphur also is combined with manganese and is generated MnS and be mingled with, and influences the low-temperature impact toughness of pipe line steel; When the oxygen element too high levels, oxide inclusion and macroscopic view are mingled with increase, and this will have a strong impact on the cleanliness factor of pipe line steel, and the oxide inclusion in the steel also is to reduce one of the HIC of steel, reason of SSC ability in the pipe line steel.Therefore, in steel of the present invention, should reduce the content of P, S, O as far as possible.Yet consider cost benefit, in the present invention, phosphorus element content is controlled by weight percentage below 0.010%, element sulphur content is controlled by weight percentage below 0.005%, oxygen element content is controlled by weight percentage below 0.002%.
In one embodiment of the invention, welding crack sensitivity coefficient Pcm=C+Si/30+ (Mn+Cu)/20+Ni/60≤0.19 of pipe line steel.
In one embodiment of the invention, described large-line energy welding has acicular ferrite structure with the X80 pipe line steel.For example, in one embodiment of the invention, the acicular ferrite among the pipe line steel X80 refers to the heterogeneous structure be made up of granular bainite, bainite ferrite and martensite-austenite structure (M-A tissue) etc.In the present invention, this acicular ferrite structure can account for more than 80% of pipe line steel X80.
In one embodiment of the invention, the described large-line energy welding yield strength Rt of X80 pipe line steel
0.2Can greater than 570MPa, tensile strength Rm can greater than 675MPa, elongation A can be greater than 20%, subzero 20 ℃ of horizontal Charpy-V impact powers can be greater than 245J, the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones can be greater than 80J under the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones under the welding analog heat input of 100KJ/cm can be greater than 126J, welding analog heat input at 200KJ/cm.
Large-line energy welding of the present invention can also be used as the high-strength engineering machines steel with the X80 pipe line steel.
The method of X80 pipe line steel of manufacturing large-line energy welding according to a further aspect of the invention said method comprising the steps of: smelting has the molten steel that the composition of X80 pipe line steel is used in above-mentioned large-line energy welding with formation; Described molten steel is cast steel billet; Rolling described steel billet, the described rolling recrystallization zone that comprises is rolling rolling with the non-recrystallization district; Cooling is through Rolled Steel, and speed of cooling is 12 ℃/s～25 ℃/s.Here, the too fast martensite that can form of speed of cooling is formed, and speed of cooling is crossed and formed bulk granular bainite and ferritic structure slowly, all is unfavorable for obtaining better comprehensive mechanical property.
In one embodiment of the invention, described method later stage that also can be included in described cooling step with the self tempering temperature control of steel in 450 ℃～550 ℃ scope.Here, self tempering temperature also can be described as water-cooled and returns red temperature, refer to that steel hot rolling enters air by water-cooled after, steel heart portion heat outwards transmits, the top temperature that the steel surface temperature recovery is reached also is self tempering temperature.It is the most effective the most direct processing parameter that influences steel tissue and performance that water-cooled is returned red temperature, and gained steel microstructure is just not different yet simultaneously for this temperature.
In one embodiment of the invention, the start rolling temperature of described recrystallization zone rolling (also can be described as roughing) can be controlled in 1150 ℃～1180 ℃ scope, its finishing temperature may be controlled to greater than 980 ℃, here, strict control roughing end temp, it is rolling to prevent that the low excessively steel billet of Yin Wendu from entering the non-recrystallization district, causes occurring mixed grain structure, and finally influences the product mechanical property.The start rolling temperature in described non-recrystallization district rolling (also can be described as finish rolling) may be controlled to be not more than 880 ℃, and its finishing temperature can be controlled in 780 ℃～820 ℃ scope, and the rolling draft in non-recrystallization district may be controlled to greater than 60%.Here, the rolling mixed grain structure that causes in the too high same meeting entering part recrystallization zone of final rolling temperature, temperature is crossed the low load that can increase milling train, and in the work-ing life of reducing milling train, therefore, the finish rolling finishing temperature is controlled in 780 ℃～820 ℃ scope.
In addition, also can carry out in the following way with the method for X80 pipe line steel according to the manufacturing large-line energy welding of another aspect of the invention, be specially:
(a) according to desired steel product ingredient configuration raw material, then with the material that configures by composition proportion, put into the 30kg vacuum induction furnace and smelt;
(b) will smelt good strand, and cut rising head, and be swaged into required blank, the forging scheme is: strand is heated to 1220 ℃, and being incubated came out of the stove after 90 minutes namely forges, and final forging temperature is not less than 1000 ℃, is swaged into the blank of 110mm (thick) * 95mm (length) * 80mm (wide);
(c) will roll the luggage stove heating of advancing through the 110mm of b technology gained (thick) * 95mm (length) * 80mm (wide) blank.When Heating temperature＞1220 ℃ can make austenite crystal sharply grow up, be unfavorable for that crystal grain thinning afterwards improves structure property, alloying element in ℃ steel of Heating temperature＜1180 can not be melted into the effect that does not have the alloying element controlled rolling and controlled cooling in the austenite fully admittedly, for this heating zone and soaking zone temperature are made as 1200 ± 20 ℃; Rate of heating surpasses 99min/cm can make defectives such as blank surface cracks be unfavorable for quality control, reduces and makes efficient, and rate of heating is controlled at 7～9min/cm; 60～120 minutes heat tracing time, the abundant solid solution of failing of too short alloying element of time, the overlong time austenite crystal can obviously be grown up;
(d) after the blank of above-mentioned c technology gained is come out of the stove, it is carried out dephosphorization process, and the blank after the dephosphorization carries out the controlled rolling of two stages, and namely the recrystallization zone is rolling rolling with the non-recrystallization district, during the recrystallization zone is rolling, start rolling temperature is 1150～1180 ℃, roughing finishing temperature＞980 ℃, here, strict control roughing end temp, it is rolling to prevent that the low excessively steel billet of Yin Wendu from entering the non-recrystallization district, causes occurring mixed grain structure, and finally influences the product mechanical property; Intermediate blank is treated temperature thickness 50mm, the rolling draft in non-recrystallization district＞60%, finish rolling start rolling temperature≤880 ℃, here, the rolling mixed grain structure that causes in the too high same meeting entering part recrystallization zone of final rolling temperature, temperature is spent the low load that can increase milling train, the work-ing life of reducing milling train, therefore, finish rolling finishing temperature control is in 780 ℃～820 ℃ scope;
(e) entering quick cooling (ACC) after the finish rolling fast controls cold, 12～25 ℃/s of cooling rate, here, the too fast martensite that can form of speed of cooling is formed, speed of cooling is crossed and is formed bulk granular bainite and ferritic structure slowly, all is unfavorable for obtaining better comprehensive mechanical property;
(f) self tempering temperature control is in 450～550 ℃ scope, and here, self tempering temperature is the most effective the most direct processing parameter that influences steel tissue and performance, and gained steel microstructure is just not different yet simultaneously for this temperature.
Embodiment 1
In the present embodiment, large-line energy welding comprises by weight percentage with the X80 pipe line steel: 0.05% carbon, 0.15% silicon, 1.5% manganese, 0.004% nitrogen, 0.012% titanium, 0.02% aluminium, 0.05% rare earth element (for example, lanthanum), 0.03% niobium, 0.2% nickel, 0.2% copper, 0.010% phosphorus, 0.005% sulphur, 0.002% oxygen and iron and other unavoidable impurities element of surplus.In the present embodiment, with the ratio basic controlling of titanium and nitrogen about 3, with the ratio basic controlling of aluminium and nitrogen about 5.
The large-line energy welding of making present embodiment may further comprise the steps with the X80 pipe line steel:
Smelting is welded with the identical molten steel of the composition of X80 pipe line steel to form with the large-line energy of present embodiment, namely in molten steel, comprise 0.05% carbon, 0.15% silicon, 1.5% manganese, 0.004% nitrogen, 0.012% titanium, 0.02% aluminium, 0.05% rare earth element, 0.03% niobium, 0.2% nickel, 0.2% copper, 0.010% phosphorus, 0.005% sulphur, 0.002% oxygen and iron and other unavoidable impurities element of surplus by weight percentage;
Described molten steel is cast steel billet;
Rolling and the next rolling described steel billet of the rolling two sections rolling modes in non-recrystallization district by the recrystallization zone;
Speed of cooling with 25 ℃/s is cooled off through Rolled Steel to room temperature.
After testing, the welding of the large-line energy of present embodiment is as follows with the salient features of X80 pipe line steel: yield strength Rt
0.2=575MPa; Tensile strength Rm=676MPa; Cross direction elongation A=23%;-20 ℃ of transverse impact merit AKv=246J; Under the welding analog heat input of 100KJ/cm, the low-temperature impact work AKv=127J of-20 ℃ of coarse-grain heat affected zones; Under the welding analog heat input of 200KJ/cm, the low-temperature impact work AKv=81J of-20 ℃ of coarse-grain heat affected zones.
Embodiment 2
In the present embodiment, large-line energy welding comprises by weight percentage with the X80 pipe line steel: 0.08% carbon, 0.35% silicon, 1.8% manganese, 0.006% nitrogen, 0.016% titanium, 0.04% aluminium, 0.08% rare earth element (for example, cerium), 0.07% niobium, 0.4% nickel, 0.5% copper, 0.005% phosphorus, 0.002% sulphur, 0.001% oxygen and iron and other unavoidable impurities element of surplus.In the present embodiment, with the weight ratio basic controlling of titanium and nitrogen about 2.67, with the weight ratio basic controlling of aluminium and nitrogen about 6.67.
The large-line energy welding of making present embodiment may further comprise the steps with the X80 pipe line steel:
Smelting is welded with the identical molten steel of the composition of X80 pipe line steel to form with the large-line energy of present embodiment, namely, this molten steel comprises 0.08% carbon, 0.35% silicon, 1.8% manganese, 0.006% nitrogen, 0.016% titanium, 0.04% aluminium, 0.08% rare earth element (for example, cerium), 0.07% niobium, 0.4% nickel, 0.5% copper, 0.005% phosphorus, 0.002% sulphur, 0.001% oxygen and iron and other unavoidable impurities element of surplus by weight percentage;
By continuous casting process described molten steel is cast steel billet;
Rolling and the next rolling described steel billet of the rolling two sections rolling modes in non-recrystallization district by the recrystallization zone, specifically, the rolling start rolling temperature in described recrystallization zone is controlled to be 1150 ℃, and its finishing temperature is controlled to be 985 ℃; The rolling start rolling temperature in described non-recrystallization district is controlled to be 880 ℃, and its finishing temperature is controlled to be 780 ℃, and the rolling draft in non-recrystallization district is controlled to be 61%,, adopts the passage rolling mode to realize rolling to steel billet here;
Cold by the ACC control, cool off through Rolled Steel with the speed of cooling of 12 ℃/s;
Self tempering temperature (be also referred to as water-cooled and the return red temperature) control of cooling off steel is about 450 ℃.
After testing, the welding of the large-line energy of present embodiment is as follows with the salient features of X80 pipe line steel: yield strength Rt
0.2=590MPa; Tensile strength Rm=680MPa; Cross direction elongation A=24%;-20 ℃ of transverse impact merit AKv=260J; Under the welding analog heat input of 100KJ/cm, the low-temperature impact work AKv=130J of-20 ℃ of coarse-grain heat affected zones; Under the welding analog heat input of 200KJ/cm, the low-temperature impact work AKv=88J of-20 ℃ of coarse-grain heat affected zones.
Embodiment 3
In the present embodiment, large-line energy welding comprises by weight percentage with the X80 pipe line steel: 0.06% carbon, 0.20% silicon, 1.6% manganese, 0.004% nitrogen, 0.016% titanium, 0.04% aluminium, 0.06% rare earth element (for example, lanthanum), 0.06% niobium, 0.3% nickel, 0.4% copper, 0.006% phosphorus, 0.003% sulphur, 0.001% oxygen and iron and other unavoidable impurities element of surplus.In the present embodiment, be 4 with the weight ratio basic controlling of titanium and nitrogen, be 10 with the weight ratio basic controlling of aluminium and nitrogen.
In the present embodiment, make large-line energy welding basic identical with among the method for X80 pipe line steel and the embodiment 2, difference is: in the present embodiment, the rolling start rolling temperature in recrystallization zone is controlled to be 1180 ℃, and its finishing temperature is controlled to be 1000 ℃; The rolling start rolling temperature in described non-recrystallization district is controlled to be 860 ℃, and its finishing temperature is controlled to be 820 ℃, and the rolling draft in non-recrystallization district is controlled to be 65%; Speed of cooling is 25 ℃/s; Self tempering temperature is controlled to be about 515 ℃.
After testing, the welding of the large-line energy of present embodiment is as follows with the salient features of X80 pipe line steel: yield strength Rt
0.2=592MPa; Tensile strength Rm=675MPa; Cross direction elongation A=22%;-20 ℃ of transverse impact merit AKv=255J; Under the welding analog heat input of 100KJ/cm, the low-temperature impact work AKv=128J of-20 ℃ of coarse-grain heat affected zones; Under the welding analog heat input of 200KJ/cm, the low-temperature impact work AKv=83J of-20 ℃ of coarse-grain heat affected zones.
Embodiment 4
In the present embodiment, the large-line energy welding comprises by weight percentage with the X80 pipe line steel: C 0.055%; Si 0.22%; Mn 1.6%; N 0.0048%; Ti 0.012%; Al 0.03%; Nb 0.04%; Ni 0.3%; Cu 0.4%; RE=0.07%; P=0.010%; S=0.005%; O=0.002%; Ti/N=2.5 wherein, Al/N=6.2, all the other are Fe and inevitable impurity.
In vacuum induction furnace, smelt and be cast into the strand of 30Kg by above composition; Strand is cut rising head, is swaged into 110mm (thick) * 95mm (length) * 80mm (wide) blank; Roll the luggage stove heating of advancing, heating zone and soaking zone temperature are 1200 ± 20 ℃, heat-up time 90min; 1170 ℃ of tapping temperatures, 1150 ℃ of roughing start rolling temperatures, 990 ℃ of roughing finishing temperatures; Intermediate blank is treated temperature thickness 50mm; 870 ℃ of finish rolling start rolling temperatures, 800 ℃ of finish rolling finishing temperatures; It is cold to enter the ACC control after the finish rolling fast, 20 ℃/s of cooling rate; Return 480 ℃ of red temperature, product thickness 12mm.
After testing, the welding of the large-line energy of present embodiment is as follows with the salient features of X80 pipe line steel: yield strength Rt
0.2=585MPa; Tensile strength Rm=684MPa; Cross direction elongation A=21%;-20 ℃ of transverse impact merit AKv=285J.Under the welding analog heat input of 100KJ/cm ,-20 ℃ of coarse-grain heat affected zone AKv=127J; Under the welding analog heat input of 200KJ/cm ,-20 ℃ of coarse-grain heat affected zone AKv=93J.
Embodiment 5
In the present embodiment, the large-line energy welding comprises by weight percentage with the X80 pipe line steel: C 0.06%; Si 0.23%; Mn 1.70%; N 0.0045%; Ti 0.015%; Al 0.02%; P 0.001%; S 0.002%; Nb 0.040%; Ni 0.24%; Cu 0.21%; RE=0.06%; Ti/N=3.3; Al/N=4.4; All the other are Fe and inevitable impurity.
In vacuum induction furnace, smelt and be cast into the strand of 30Kg by above composition; Strand is cut rising head, is swaged into 110mm (thick) * 95mm (length) * 80mm (wide) blank; Roll the luggage stove heating of advancing, heating zone and soaking zone temperature are 1200 ± 20 ℃, heat-up time 90min; 1170 ℃ of tapping temperatures, 1150 ℃ of roughing start rolling temperatures, 990 ℃ of roughing finishing temperatures; Intermediate blank is treated temperature thickness 50mm; 870 ℃ of finish rolling start rolling temperatures, 800 ℃ of finish rolling finishing temperatures; It is cold to enter the ACC control after the finish rolling fast, 15 ℃/s of cooling rate; Return 465 ℃ of red temperature, product thickness 12mm.
After testing, the welding of the large-line energy of present embodiment is as follows with the salient features of X80 pipe line steel: yield strength Rt
0.2=571MPa; Tensile strength Rm=678MPa; Cross direction elongation A=23%;-20 ℃ of transverse impact merit AKv=248J; Under the welding analog heat input of 100KJ/cm ,-20 ℃ of coarse-grain heat affected zone AKv=132J; Under the welding analog heat input of 200KJ/cm ,-20 ℃ of coarse-grain heat affected zone AKv=82J.
In sum, remove Cr, Mo precious metal element on the basis that the present invention adopts low Carbon Manganese to be, can be by adding the X80 pipe line steel that can satisfy the large-line energy welding operation that microalloy element, control Ti/N and means such as Al/N and controlled rolling and controlled cooling such as proper amount of rare-earth obtain to have needle-like voxel body tissue, the intensity of this X80 pipe line steel, good-toughness also can satisfy under the big welding heat input of 200KJ/cm requirement to its plate of moderate thickness coarse-grain heat affected zone (CGHAZ) low-temperature impact toughness.In addition, large-line energy welding of the present invention is low with X80 pipe line steel cost.
Although above by having described the present invention in conjunction with exemplary embodiment, it will be apparent to those skilled in the art that under the situation that does not break away from the spirit and scope that claim limits, can carry out various modifications and change to exemplary embodiment of the present invention.
Claims (10)
1. a large-line energy welds and uses pipe line steel, it is characterized in that, described large-line energy welding comprises by weight percentage with pipe line steel: 0.05%～0.08% carbon, 0.15%～0.35% silicon, 1.5%～1.8% manganese, 0.004%～0.006% nitrogen, 0.012%～0.016% titanium, 0.02%～0.04% aluminium, 0.05%～0.08% rare earth element, 0.03%～0.07% niobium, 0.2%～0.4% nickel, 0.2%～0.5% copper, be not more than 0.010% phosphorus, be not more than 0.005% sulphur, be not more than iron and other unavoidable impurities element of 0.002% oxygen and surplus, wherein the control of the weight ratio of titanium and nitrogen is between 2～4, the weight ratio control of aluminium and nitrogen is between 3～10, make and form Ti in the steel, Al, the complex inclusion of N, described complex inclusion has stable performance under 1370 ℃ high temperature, the described large-line energy welding yield strength Rt of pipe line steel
0.2Greater than 570MPa, the welding of described large-line energy with pipe line steel the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones under the welding analog heat input of 100KJ/cm greater than 126J, welding analog heat input at 200KJ/cm under the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones greater than 80J.
2. pipe line steel is used in large-line energy welding as claimed in claim 1, it is characterized in that welding crack sensitivity coefficient Pcm=C+Si/30+ (Mn+Cu)/20+Ni/60≤0.19 of described pipe line steel.
3. pipe line steel is used in large-line energy welding as claimed in claim 1 or 2, it is characterized in that, described large-line energy welding has acicular ferrite structure with pipe line steel.
4. pipe line steel use in large-line energy as claimed in claim 3 welding, it is characterized in that, the tensile strength Rm of described large-line energy welding usefulness pipe line steel greater than 675MPa, elongation A greater than 20%, subzero 20 ℃ of horizontal Charpy-V impact powers are greater than 245J.
5. pipe line steel is used in large-line energy welding as claimed in claim 1, it is characterized in that, described large-line energy welding can be used as the non-pipe line steel that requires the large-line energy welding with pipe line steel.
6. pipe line steel is used in large-line energy welding as claimed in claim 5, it is characterized in that, described large-line energy welding can be used with steel as high-strength engineering machines with pipe line steel.
7. make the large-line energy welding with the method for pipe line steel for one kind, it is characterized in that, said method comprising the steps of:
Smelting has the molten steel that the composition of pipe line steel is used in the described large-line energy welding of claim 1 with formation;
Described molten steel is cast steel billet;
Rolling described steel billet, the described rolling recrystallization zone that comprises is rolling rolling with the non-recrystallization district;
Cooling is through Rolled Steel, and speed of cooling is 12 ℃/s～25 ℃/s,
Wherein, be formed with the complex inclusion of Ti, Al, N in the described pipe line steel, described complex inclusion has stable performance under 1370 ℃ high temperature, described pipe line steel the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones under the welding analog heat input of 100KJ/cm greater than 126J, welding analog heat input at 200KJ/cm under the low-temperature impact work AKv of subzero 20 ℃ of coarse-grain heat affected zones greater than 80J.
8. manufacturing large-line energy welding as claimed in claim 7 is characterized in that with the method for pipe line steel, and described method also comprises to be controlled the self tempering temperature of steel in 450 ℃～550 ℃ scope.
9. manufacturing large-line energy welding as claimed in claim 7 is characterized in that with the method for pipe line steel, and the rolling start rolling temperature in described recrystallization zone is controlled in 1150 ℃～1180 ℃ scope, and its finishing temperature is controlled to be greater than 980 ℃; The rolling start rolling temperature in described non-recrystallization district is controlled to be and is not more than 880 ℃, and its finishing temperature control is in 780 ℃～820 ℃ scope, and the rolling draft in non-recrystallization district is controlled to be greater than 60%.
10. manufacturing large-line energy welding as claimed in claim 7 is characterized in that with the method for pipe line steel, the described step employing continuous casting process of molten steel being cast steel billet.
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| KR101726082B1 (en) * | 2015-12-04 | 2017-04-12 | 주식회사 포스코 | Steel having superior brittle crack arrestability and resistance brittle crack initiation of welding point and method for manufacturing the steel |
| CN111286672B (en) * | 2020-03-25 | 2022-03-29 | 江苏省沙钢钢铁研究院有限公司 | Needle-shaped ferrite type X60-grade HIC-resistant pipeline steel and rolling method thereof |
| CN113046653B (en) * | 2021-02-01 | 2022-03-01 | 南京钢铁股份有限公司 | Pipeline steel with excellent high heat input welding performance and manufacturing method thereof |
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| CN101845596A (en) * | 2009-03-24 | 2010-09-29 | 宝山钢铁股份有限公司 | Wide thick plate for X80 pipe line steel and manufacturing method thereof |
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Effective date of registration: 20220708 Address after: 271104 Shuangquan Road, Gangcheng District, Jinan City, Shandong Province Patentee after: LAIGANG GROUP YINSHAN SHAPED STEEL Co.,Ltd. Address before: Friendship Street 271100 Shandong province Laiwu City Gangcheng District No. 38 Patentee before: LAIWU STEEL Group Ltd. |