CN105586529A - 890MPa-level high-strength steel, steel pipe and manufacturing method of steel pipe - Google Patents
890MPa-level high-strength steel, steel pipe and manufacturing method of steel pipe Download PDFInfo
- Publication number
- CN105586529A CN105586529A CN201610105103.3A CN201610105103A CN105586529A CN 105586529 A CN105586529 A CN 105586529A CN 201610105103 A CN201610105103 A CN 201610105103A CN 105586529 A CN105586529 A CN 105586529A
- Authority
- CN
- China
- Prior art keywords
- steel
- steel pipe
- 890mpa
- strength
- temperature
- 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.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses 890MPa-level high-strength steel. The 890MPa-level high-strength steel is prepared from the chemical elements including, by mass, 0.12-0.18% of C, 0.1-0.4% of Si, 0.8-1.4% of Mn, 0.5-0.9% of Cr, 0.20-0.60% of Mo, 0.01-0.08% of W, 0.50-1.30% of Ni, 0.01-0.06% of Nb, 0.03-0.12% of V, 0.01-0.05% of Al and 0.0005-0.005% of Ca, and the relational expression that 5<Ni/(C*Mo)<=50 is applicable. The invention further discloses a steel pipe which is made from the 890MPa-level high-strength steel in the scheme. The invention further discloses a manufacturing method of the steel pipe. The manufacturing method includes the steps that the steel is made and cast into a round blank; the round blank is heated; high-pressure water is used for removing scale; pipe rolling is performed; quenching-and-tempering heat treatment is performed; high-pressure water is used for removing scale; hot straightening is performed.
Description
Technical field
The present invention relates to a kind of alloy steel products and manufacture method thereof, relate in particular to a kind of high-strength alloy steelAnd manufacture method.
Background technology
Current engineering machinery and steel construction piece are towards large load-bearing, light-weighted future development. Lightweight directionBe to improve the strength of materials, not only can reduce the deadweight of structure, save material, be also conducive to improve structureIntegrated carrying ability. But, for the steelwork component that bears top load, in order to improve steel pipeResisting longitudinal unstability ability, ensure the high-intensity while, also needing has enough thickness, for example, thisMore than the wall thickness of class steel construction will reach 16mm. But, the properties of product of heavy caliber thick wall high strength steel pipeOften fluctuating range is larger, and intensity and toughness are often difficult to take into account simultaneously.
Along with improving constantly of construction machinery product Performance and quality, the continuous enhancing of bearing capacity, market butt weldingConnect the superhigh intensity of function admirable, the demand cumulative year after year of thick-walled structure steel pipe, solve solderability strong, highThe production manufacturability problem of strong high tenacity, thick-walled structure steel pipe is very urgent. For example, publication number isCN102747300A, open day is on October 24th, 2012, name is called " a kind of high-strength and high-ductility structureBy seamless steel pipe and manufacture method thereof " Chinese patent literature a kind of high-strength and high-ductility structure nothing is disclosedSeam steel pipe and manufacture method thereof. This manufacture method comprises smelting molten steel, continuous casting, tube rolling unit rolling step,Wherein, smelting molten steel step obtains target molten steel, and the composition of target molten steel is by weight percentage:C：0.14～0.18％，Si：0.20～0.50％，Mn：0.90～1.30％，P≤0.020％，S≤0.010％，Cr：0.20～1.00％，Mo：0.20～0.80％，Ni：0.90～1.50％，V：0.02～0.10％，Nb≤0.05%, Al:0.015～0.050%, Cu≤0.35%, N≤0.020%, Ti≤0.05%, surplus isIron and inevitably impurity. Above-mentioned manufacture method also comprises modified heat treatment step, at described tube rollingAfter unit rolling step, steel pipe order is quenched and temper, wherein, hardening heat is 920～960 DEG C, temperature is 610～660 DEG C. Because this section of disclosed seamless steel pipe of patent documentation contains veryThe Ni element of high-load, the oxide skin that is formed at steel tube surface in postorder production process is difficult to get rid of,Have a strong impact on steel tube surface quality.
Again for example, publication number is CN101397640A, and open day is on April 1st, 2009, and name is called " bendsTake intensity 960MPa level welded structural steel " Chinese patent literature a kind of yield strength 960MPA is disclosedLevel welded structural steel, its each chemical constituent and percentage by weight are: C:0.14～0.19, Si:0.15～0.40,Mn:1.40～<1.7，Mo:0.41～0.60，B:0.0005～0.002，Cr:0～0.50，Ni:0～0.40，Nb:0～0.03, Ti:0.010～0.050, Als:0.01～0.06, P≤0.020, S≤0.010, all the other areFe and inevitable impurity; Meet: carbon equivalent ce V (%) < 0.65 or PCM (%) < 0.35 simultaneously.Although the level that the yield strength of the disclosed welded structural steel of this patent documentation can reach 890MPa withUpper, but-20 DEG C of ballistic works of this welded structural steel are only 52J.
Publication number CN104862613A, open day is on August 26th, 2015, name is called " a kind of high strengthSteel, high tensile steel tube and manufacture method thereof " Chinese patent literature related to a kind of high strength steel, its changeLearning element mass percentage content is: C:0.11-0.18%, and Si:0.1-0.4%, Mn:1.0-1.6%,Cr：0.25-0.9％，Mo：0.10-0.50％，W：0.10-0.55％，Nb：0.01-0.08％，V：0.01-0.12％，Ni:0.10-0.40％，0<B<0.0020％，0＜N≤0.004％，0<Ti≤0.010％，O < 0.0030%, S < 0.005%, Ca+Mg:0.001-0.005%, surplus is that Fe is inevitable with otherImpurity. In this Chinese patent literature, in disclosed high strength steel, added W element, it can haveEffect ground promotes the intensity of Steel material, makes the tensile strength > 980MPa of Steel material, and is improving intensityTime, comparing to other alloying elements (for example, Mo element), W reduces the journey of the welding performance of steelSpend relatively low. But, owing to having added the W of certain content, increase on the one hand thus steel-making difficulty,Improve the difficulty of manufacturing, made on the other hand the Steel material after shrend easily bending, even temperingAfter be also difficult to aligning.
Under the prerequisite of intensity of guaranteeing Steel material, in order to reduce the difficulty of manufacturing process process, andImprove plate shape and the surface quality of Steel material, enterprise needs acquisition one badly and has high-strength tenacity and weldability concurrentlySteel material, to adapt to the manufacturing of thick-walled structure steel pipe. In addition, this Steel material also needs to have excellentGood surface quality and good plate shape,
Summary of the invention
The object of the present invention is to provide a kind of 890MPa grade high-strength steel, this 890MPa grade high-strengthSteel has higher intensity, good quenching degree, good low-temperature flexibility and excellent welding performance.In addition, 890MPa grade high-strength steel of the present invention also has good surface quality and plate shape concurrently.
To achieve these goals, the invention provides a kind of 890MPa grade high-strength steel, its chemistry unitQuality amount per distribution ratio is:
C：0.12-0.18％；
Si：0.1-0.4％；
Mn：0.8-1.4％；
Cr：0.5-0.9％；
Mo：0.20-0.60％；
W：0.01-0.08％；
Ni：0.50-1.30％；
Nb：0.01-0.06％；
V：0.03-0.12％；
Al：0.01-0.05％；
Ca：0.0005-0.005％；
Also meet following relational expression: 5 < Ni/ (C*Mo)≤50 simultaneously;
Surplus is Fe and other inevitable impurity.
The design principle of the each chemical element in 890MPa grade high-strength steel of the present invention is:
Carbon: C is the necessary chemical composition of guaranteeing matrix strength. If the content of C is lower than 0.12%, justCan not obtain desired intensity. If the content of C is higher than 0.18%, can by what affect high strength steelWeldering property, and cause lower toughness in the part being influenced by heat of steel. Given this, of the present inventionIn 890MPa grade high-strength steel, controlling C content is 0.12-0.18%.
Silicon: Si in steel as deoxidier. In order to reach deoxidation effect, in high strength of the present inventionIn steel, at least need to add more than 0.1% Si. But, once Si content cross can reduce at most steel canWeldering property and toughness. Consider the combination property of deoxidation effect and steel, need to be by above-mentioned high strength steelThe control of Si content is 0.1-0.4%.
Manganese: Mn in steel also as a kind of deoxidier. Meanwhile, high in order to ensure above-mentioned 890MPa levelStrength steel has good intensity and low-temperature flexibility concurrently, and Mn content need to reach more than 0.8%. But, mistakeMany Mn elements also can increase the quenching degree of steel, not only can reduce HAZ (heat affected area) tough of steelProperty and solderability, and produce center segregation can cause casting continuously time, the low-temperature flexibility of mother metal also can be withDeterioration. Therefore, the Mn content in 890MPa grade high-strength steel of the present invention should be controlled and be0.8-1.4％。
Chromium: Cr can increase the intensity of mother metal, welding position, and improves the quenching degree of steel. If Cr containsMeasure too high, both can make weld cracking sensitiveness increase, can reduce again the toughness of welding heat affected zone. SoAnd Cr content is too low, its effect that can play is also not obvious. For this reason, by above-mentioned 890MPa levelThe content of Cr in high strength steel is set as 0.5-0.9%.
Molybdenum: Mo is also one of main adding elements of the present invention, and it can improve the hardenability of steel. Meanwhile,Reinforced alloys elements Mo can improve the intensity of Steel material effectively. In addition, Mo is at high-temperature oxydation ringIn border, easily form high-volatile molybdenum trioxide, can effectively improve the adhesion of oxide skin, make itUnder water under high pressure, be easy to peel off. But, the HAZ toughness of adding too much Mo and also can reduce steel, forReach best strengthening effect, and improve the surperficial oxide skin situation of steel, need to be by the control of Mo contentBetween 0.20-0.60% scope.
Tungsten: the interpolation of W element can advantageously improve the hardenability of steel. In improving the intensity of steel,W compares to other alloy principles (for example, Mo element), and the degree of the welding performance of its reduction steel is lower., add too much W and not only can significantly increase steel-making difficulty, improve production cost, but also can makeObtain steel and be easy to bending in shrend, after tempering, be difficult to aligning. In technical scheme of the present invention, particularly needTo strictly control for W element, be controlled between 0.01-0.08% scope by its content.
Nickel: Ni is one of main adding elements of the present invention, not only can effectively improve quenching of thick walled steel tubeThoroughly property, can also improve low-temperature flexibility and the on-the-spot solderability of material. Compare to add Mn, Cr orThe elements such as Mo, add Ni and can not form the sclerotic tissue that is unfavorable for low-temperature flexibility. If Ni addition mistakeFew, its effect is not remarkable, if Ni addition is too much, and the oxide skin generating in manufacturing processRemoving difficulty increases. Based on technical scheme of the present invention, by the Ni content in 890MPa grade high-strength steelBe set as 0.5-1.3%.
Niobium and vanadium: Nb is the important element that obtains fine-grained steel, and it can postpone austenite and tie in the time of hot rollingBrilliant and reach the object of crystal grain thinning. In cooling and course of hot rolling subsequently, NbC particle dispersion is separated out,Can play again the effect of precipitation strength. In heating process again, can hinder again Austenite Grain Growth.V has the effect similar with Nb, but its effect than Nb a little less than some. But, in high strength steel, addAdd the precipitating reinforcing effect that V produces larger, the compound interpolation of Nb and V can make of the present invention890MPa grade high-strength steel obtain more good comprehensive mechanical property. Consider heat affected areaToughness and on-the-spot solderability, the content of Nb and V all can not be too high. Based on technical side of the present inventionCase, Nb content should be controlled as 0.01-0.06%, and V content should be controlled as 0.03-0.12%.
Aluminium: Al has deoxidation in steel, and it is conducive to improve toughness and the processing characteristics of steel.When Al content reaches 0.01% when above, its improve toughness of steel and the effect of processing characteristics comparatively remarkable.But if Al content exceedes 0.05%, steel-making difficulty obviously increases. Based on this, of the present inventionIn 890MPa grade high-strength steel, Al content need to be controlled between 0.01-0.05% scope.
Calcium: Ca can cleaning molten steel, makes inclusion modification to control the distributional pattern of steel medium sulphide content,Reach the object that obtains tiny spherical, sulfide that disperse is uniform, thereby play the work that improves low-temperature flexibilityWith. For 890MPa grade high-strength steel of the present invention, Ca content should be controlled and be0.0005-0.005％。
In the technical program, in order to reduce steel-making difficulty and to avoid steel easily to bend after shrend,Key is to control the content of W. Comparing to publication number is CN104862613A, and open day is 2015On August 26,, it is special that name is called China of " a kind of high strength steel, high tensile steel tube and manufacture method thereof "The content of W in the disclosed high strength steel of profit document, the W content phase in technical scheme of the present inventionTo lower, but this can weaken W and improve the hardenability of steel and the beneficial effect of intensity. For make up because ofThe minimizing of W element addition and cause this deficiency, the corresponding Ni unit that increased of technical scheme of the present inventionThe addition of element. That is to say, technical scheme of the present invention compares to existing technical scheme and has adopted and fallW rises the favourable measure of Ni, takes full advantage of the element synergy between W and Ni.
The lattice paprmeter of Ni Yu γ ?iron close, can form continuous solid solution, be so just conducive to improveThe hardenability of thick walled steel tube. Meanwhile, because Ni can reduce critical point and increase austenitic stability,Therefore its hardening heat can be further reduced, and quenching degree is good, quenches and is not easy bending.
But inventor's further discovery again, the Ni that adds high-load can make steel tube surface generation thickerOxide skin, and easily there is the problem that oxide skin adheres to. This is because Ni is that one is more dysoxidizable in steelElement generally needs to experience 1250 DEG C of left and right heating of pipe blank and 900 DEG C of tune in steel tube regeneration product processTwice high-temperature oxidation process such as matter heat treatment, when especially heating in 1250 DEG C of left and right heating of pipe blank processesBetween will reach 2-4h, steel tube surface often can form thicker oxide skin. In this heating process, FePreferential oxidation, the enrichment that just produces Ni at iron scale internal layer, forms metal twine and the particle of rich Ni,And be in wedge shape immersion metallic matrix, to have increased the adhesiveness containing the iron scale of Ni steel. Meanwhile, withThe adhesiveness of the rising iron scale of temperature will increase. The metal twine of this rich Ni is iron scaleLink up with metallic matrix, because its plasticity is similar with metallic matrix with performance parameters such as thermal coefficient of expansions,Even if therefore, under the impact of water under high pressure, be still not easy to peel off. In this case, adding containing Ni steelThe iron scale forming in thermal process is difficult to remove, and will in follow-up perforation, tube rolling process, produceSurface scale defect, thus cause steel tube surface presentation quality poor, need reconditioning quality large, the production cycle is long,Production cost increases, and is difficult to many unfavorable defects such as guarantee delivery date.
For these reasons, the technical program, in the situation that improving Ni constituent content, also defines relationFormula 5 < Ni/ (C*Mo)≤50, to obtain good scale removal effect, contains thereby effectively avoid adding heightThe iron scale adhesiveness phenomenon that the Ni of amount brings. C and Mo are all effectively strengthening units for steelElement. In addition, Mo can also improve the hardenability of steel, and easily forms high waving in high-temperature oxidation environmentThe molybdenum trioxide of the property sent out, effectively to reduce the adhesion of iron scale, makes it under the impact of water under high pressureBe easy to peel off, make iron scale be difficult to adhere to steel material surface, thereby improve the surperficial matter of Steel materialAmount.
Further, the microstructure of 890MPa grade high-strength steel of the present invention is tempered sorbite.
Further, the carbon equivalent Ceq=C+Mn/6+ of 890MPa grade high-strength steel of the present invention(Cr+Mo+V)/5+Ni/15≤0.65。
Carbon equivalent Ceq is controlled to≤0.65, be conducive to improve the welding performance of Steel material, reduce welding pre-Hot temperature degree, reduces weld defect. Once carbon equivalent Ceq exceedes 0.65, welding pre-heating temperature will soExceed 150 DEG C, be unfavorable for the field sizeization manufacturing.
Further, in 890MPa grade high-strength steel of the present invention, other are inevitably assortedP < 0.013% in matter, S≤0.005%.
In the technical program, inevitably impurity mainly refers to P element and S element. For of the present inventionTechnical scheme, P element and S element are harmful elements, their content in steel needs more more lowWell, still consider the economy of smelting iron and steel cost, therefore, can be by the content control of S element≤ 0.005%, and be < 0.013% by the content control of P element.
Further, the yield strength of 890MPa grade high-strength steel of the present invention be greater than 890MPa,The low-temperature impact toughness that tensile strength is greater than at 960MPa ,-40 DEG C is greater than 100J.
Based on technique scheme, this high strength steel has higher intensity and good low-temperature flexibility concurrently.
890MPa grade high-strength steel of the present invention by the appropriate Ni of compound interpolation, Mo, Cr, V,The alloying elements such as Nb, utilize the measure of falling W and rising Ni, and by the collaborative work of the element between W and NiWith, utilize relational expression 5 < Ni/ (C*Mo)≤50 to limit the best proportioning between Ni and C, Mo,Not only make Steel material after heating process, under water under high pressure effect, just can effectively remove steelExpect surperficial iron scale, also reduce steel-making difficulty and avoid Steel material very easily to occur after shrend operationBending, has improved the surface quality of Steel material thus, and has improved the plate shape of Steel material. Moreover, thisBright described 890MPa grade high-strength steel obtains having tempered sorbite microcosmic group after by heat treatment stepThe Steel material of knitting, and utilize the solution strengthening of alloying element and precipitation strength to improve the strength of parent of material,Make Steel material keep the high-intensity good low-temperature flexibility that simultaneously also has. Based on this, by thisBright technical scheme and obtain and there is higher-strength, better low-temperature flexibility, excellent surface quality and goodThe 890MPa grade high-strength steel of welding performance.
Another object of the present invention is to provide a kind of steel pipe. This steel pipe possesses higher intensity, goodQuenching degree and good low-temperature flexibility. In addition, steel pipe of the present invention has excellent welding performance,Steel pipe pipe fitting is difficult for bending. In addition, the iron scale adhesiveness of steel tube surface of the present invention is low, holdsEasy-clear, makes steel pipe have good surface quality. Meanwhile, this steel pipe is suitable as and bears top loadStructural steel pipe.
In order to reach foregoing invention object, steel pipe proposed by the invention adopts any as mentioned aboveA kind of 890MPa grade high-strength steel and making.
The obdurability index of the welding point after steel-pipe welding of the present invention and heat affected area can reachThe obdurability index level of pipe fitting mother metal.
Correspondingly, the present invention also provides a kind of manufacture method of above-mentioned steel pipe. Can by this manufacture methodHigh to obtain intensity, quenching degree is good, the steel pipe that low-temperature flexibility energy is good and welding performance is excellent. In addition,The excellent surface quality of the steel pipe obtaining by this manufacture method, steel pipe pipe fitting is difficult for bending. In addition, originallyThe manufacture method of invention is suitable for manufacturing the steel pipe that tube wall is thicker.
In order to realize foregoing invention object, the manufacture method of a kind of steel pipe that the present invention proposes, it comprises stepRapid:
(1) make steel and be cast into round base;
(2) justify base heating;
(3) high-pressure water descaling;
(4) tube rolling, rolls rear air cooling;
(5) modified heat treatment: hardening heat is 880-930 DEG C, temperature retention time is 30-60min, soRear shrend. Carry out high tempering at 580-650 DEG C, temperature retention time is 30-80min;
(6) high-pressure water descaling;
(7) thermal straightening: the control of thermal straightening temperature is 500-600 DEG C.
The key of above-mentioned manufacture method is modified heat treatment step. By controlling in modified heat treatment stepHardening heat and temperature retention time, after shrend, in steel pipe, form martensite microstructure. Meanwhile,At 580-650 DEG C of temperature, carry out high tempering, and to control temperature retention time be 30-80min, to make horseFamily name's body microstructure forms tempered sorbite microstructure under high tempering state, thereby order has, this is micro-See the steel pipe of tissue in possessing higher-strength, also have the comprehensive mechanics such as good toughness and plasticity concurrentlyPerformance.
Due to lower in the temperature of adjusting the high tempering in heat treatment step, temperature retention time is relatively short again,Therefore the iron scale forming in steel tube surface can be removed by follow-up high-pressure water descaling operation, can notOn steel pipe, producing iron scale adheres to.
Moreover, in order effectively to avoid steel pipe to occur serious flexural deformation, in thermal straightening operation, controlThermal straightening temperature is 500-600 DEG C.
Further, the manufacture method of steel pipe of the present invention also comprises step (8) welding: adopt gasBody shielded arc welding is by welding after some sections of steel pipe docking, and welding wire deposited metal tensile strength is not less than960MPa, to ensure that welding point has higher tensile strength, preheat temperature 90-150 DEG C, to preventThere is HAZ cold crack in steel pipe.
Further, in above-mentioned steps (2), control firing rate 9-11min/cm, soaking temperatureFor 1220-1240 DEG C and insulation 60-120min.
Once inventor finds that soaking temperature reaches more than 1250 DEG C in heating steps, steel pipe iron scaleViscosity just increase, even if iron scale can not be got rid of by high pressure water impact. For this reason, in heatingIn step, soaking temperature is controlled between 1220-1240 DEG C, like this, iron scale can pass through substantiallyWater under high pressure is removed, thereby has improved the surface quality of steel pipe.
Further, in above-mentioned steps (3), control water under high pressure pressure and be greater than 10MPa, to obtainGood scale removal effect, removes the iron scale that is formed at steel tube surface, effectively to avoid it to be pressed intoSteel tube surface and produce mass defect, thus the surface quality of tube product improved. In the technical program,Controlling water under high pressure pressure is greater than 10MPa and refers to that water under high pressure pressure just can realize this technology higher than 10MPaScheme, and do not control in the upper-bound theory of water under high pressure pressure. But, the technology people in this areaMember know, for the reason of economical and energy saving, this upper limit can not be generally unconfined height yet, should give birth toProduce in permission or attainable scope.
Further, in above-mentioned steps (4), controlling finish to gauge rolling temperature is 950-1050 DEG C.
Finish to gauge rolling temperature is controlled to object between 950-1050 DEG C and is to make the austenite crystal of distortionAfter grain hot rolling, complete in time dynamic recrystallization, and form evenly tiny equiax crystal, then obtain uniformlyRoll state tissue, provide organizational structures for subsequent heat treatment obtains good performance.
Further, in above-mentioned steps (6), control water under high pressure pressure and be greater than 6MPa, good to obtainGood scale removal effect, removes the iron scale that is formed at steel tube surface, effectively to avoid it to be pressed into steelTube-surface and produce mass defect, thus the surface quality of tube product improved. In the technical program,Controlling water under high pressure pressure is greater than 6MPa and refers to that water under high pressure pressure just can realize this technical side higher than 6MPaCase, and do not control in the upper-bound theory of water under high pressure pressure. But, those skilled in the artKnow, for the reason of economical and energy saving, this upper limit can not be generally unconfined height yet, should produceIn permission or attainable scope.
The intensity of 890MPa grade high-strength steel of the present invention is high, and its yield strength is greater than 890MPaAnd tensile strength is greater than 960MPa.
In addition, 890MPa grade high-strength steel of the present invention has good low-temperature flexibility and excellence concurrentlyWelding performance, the low-temperature impact toughness at its-40 DEG C is greater than 100J.
In addition, compare to existing high strength steel, the W of 890MPa grade high-strength steel of the present inventionContent reduces, and Ni content increases, and has advantageously avoided steel plate bending, has improved steel-plate shape, effectivelyAvoid iron scale to adhere to, improved the surface quality of steel plate.
Steel pipe of the present invention has higher intensity, good low-temperature flexibility and good welding performance,Its mother metal yield strength is greater than 890MPa, and tensile strength is greater than 960MPa, the low-temperature impact at-40 DEG CToughness is greater than 100J, and the welding point tensile strength after welding is greater than 960MPa, the low temperature of heat affected areaMore than toughness reaches 80J.
Can obtain intensity by the manufacture method of steel pipe of the present invention high, quenching degree is good, low temperatureThe steel pipe of tough function admirable and welding performance excellence.
In addition, the excellent surface quality of the steel pipe obtaining by the manufacture method of steel pipe of the present invention,Steel pipe pipe fitting is difficult for bending.
In addition, the manufacture method of steel pipe of the present invention is suitable for manufacturing the steel pipe that tube wall is thicker.
Brief description of the drawings
Fig. 1 is the shape appearance figure of the iron scale of the steel tube surface of embodiment A 1.
Fig. 2 is the shape appearance figure of the iron scale of the steel tube surface of comparative example B1.
Fig. 3 is the shape appearance figure of the iron scale of the steel tube surface of comparative example B2.
Detailed description of the invention
Below will be according to specific embodiment to 890MPa grade high-strength steel of the present invention, steel pipe andManufacture method is made and being further illustrated, but specific embodiment and related description do not form for the present inventionThe improper restriction of technical scheme.
Embodiment A 1-A7 and comparative example B1-B4
Manufacture the steel pipe in embodiment and comparative example according to following step, it comprises:
(1) steel-making: smelt refining, vacuum outgas, and control the matter of the each chemical element in molten steelAmount per distribution ratio is as shown in table 1;
(2) be cast into round base;
(3) justify base heating: control firing rate 9-11min/cm, soaking temperature is 1220-1240 DEG CAnd insulation 60-120min;
(4) high-pressure water descaling: control water under high pressure pressure and be greater than 10MPa;
(5) tube rolling: perforation tube rolling, to roll rear air cooling and carry out sawing, control finish to gauge rolling temperature is950-1050℃；
(6) modified heat treatment: hardening heat is 880-930 DEG C, temperature retention time is 30-60min,Then shrend. Carry out high tempering at 580-650 DEG C, temperature retention time is 30-80min,To ensure that steel pipe obtains good comprehensive mechanical property;
(7) high-pressure water descaling: control water under high pressure pressure and be greater than 6MPa;
(8) thermal straightening: the control of thermal straightening temperature is 500-600 DEG C;
(9) welding: adopt gas shielded arc welding by welding after some sections of steel pipe docking, welding wire is moltenMetallisation tensile strength is not less than 960MPa, and preheat temperature 90-150 DEG C, to preventThere is HAZ cold crack in steel pipe.
In above steps, concrete technology parameter is in detail referring to table 2.
Table 1 has been listed the matter of the each chemical element in the steel pipe of embodiment A 1-A7 and comparative example B1-B4Amount per distribution ratio.
Table 1. (wt.%, surplus is Fe and other the inevitable impurity except P and S)
* note: relational expression is: 5 < Ni/ (C*Mo), Ceq=C+Mn/6+ (Cr+Mo+V)/5+Ni/15.
Table 2 has been listed the technique ginseng of the manufacture method of the steel pipe of embodiment A 1-A7 and comparative example B1-B4Number.
Table 2.
At room temperature, for measuring after embodiment A 1-A7 and comparative example B1-B4 sampling, wherein,Carry out-40 DEG C of pendulum impact tests for the welding point of above-mentioned steel pipe, to measure rushing of its heat affected areaHit performance, and relevant mechanical property parameters is listed in table 3.
Table 3 has been listed the mechanical property parameters of the steel pipe in embodiment A 1-A7 and comparative example B1-B4.
Table 3.
As can be seen from Table 3, embodiment A 1-A7 yield strength all >=948MPa, tensile strength all >=998MPa, percentage elongation >=15%, impact flexibility (40 DEG C) AKv >=106J, HAZ toughness (40 DEG C)AKv >=84J, welding point tensile strength >=985MPa, as can be seen here, the steel pipe in above-described embodimentYield strength be all greater than 890MPa, tensile strength is all greater than 960MPa, the low-temperature impact at-40 DEG C is toughProperty be all greater than 100J, the HAZ impact flexibility at-40 DEG C is all greater than 80J, thus the steel pipe tool of explanation this caseStandby higher intensity, simultaneously with good low-temperature flexibility, good plasticity and excellent welding performance.Review, in the steel pipe of comparative example B1-B4, all have chemical element to exceed scope, particularly, comparative example B1In C element, the Ni element in comparative example B2, the Mo element in comparative example B3-B4 has all exceededThe scope limiting, even if comparative example B1-B4 adopts identical technological parameter, and this technological parameter is notExceed the scope of restriction, but the intensity of the steel pipe of comparative example B1-B4 or toughness index do not reach this caseThe level requiring. Wherein, the mother metal tensile strength of comparative example B1, B3 and B4 and welding point tension are strongDegree is all no more than 960MPa, and the mother metal yield strength of comparative example B3 and B4 does not reach 890MPa level yetLevel, impact flexibility (40 DEG C) AKv of comparative example B2 is only 27J, HAZ toughness (40 DEG C)AKv is only 15J.
To naturally cooling after embodiment A 1, comparative example B1 and comparative example B2 sampling heating, observe respectively realExecute the pattern of the iron scale of example and comparative example.
Fig. 1, Fig. 2 and Fig. 3 have shown respectively the steel of embodiment A 1, comparative example B1 and comparative example B2The pattern of the iron scale of tube-surface.
As shown in Figure 1, consult if desired table 1, the outer oxide iron sheet of the steel tube surface of embodiment A 1 is dredgedPine porous, internal layer adhesion layer is thinner, easily gets rid of by high pressure water impact.
As shown in Figure 2, consult if desired table 1, because the Ni/ (C*Mo) of comparative example B1 is 65,It exceedes 50, that is to say, the proportion relation between Ni element and C, Mo does not meet the limit of relational expressionFixed, therefore, the internal layer adhesion layer of the steel tube surface of comparative example B1 is thicker, even if pass through high pressure water flushingHit and be also difficult to remove the iron scale that is attached to steel tube surface.
As shown in Figure 3, consult if desired table 1, although the internal layer adhesion layer of comparative example B2 is thinner, easilyDispose by high pressure water impact, but because Ni element has exceeded limited range, and Ni element and C,Proportion relation between Mo does not meet the restriction of relational expression, therefore, the low-temperature flexibility of comparative example B2 andHAZ toughness is lower, does not meet the mechanical property level that this case requirement reaches.
The manufacture method of steel pipe of the present invention is especially applicable to manufacturing the thicker steel pipe of tube wall, and this steelPipe can be applied to relevant manufacturing field as the structural steel pipe of carrying top load.
It should be noted that above enumerate only for specific embodiments of the invention, obviously the present invention does not limitIn above embodiment, there are many similar variations thereupon. If those skilled in the art is from the present inventionAll distortion that disclosed content directly derives or associates, all should belong to protection scope of the present invention.
Claims (11)
1. a 890MPa grade high-strength steel, its chemical element quality per distribution ratio is: C:0.12-0.18%,Si：0.1-0.4％，Mn：0.8-1.4％，Cr：0.5-0.9％，Mo：0.20-0.60％，W：0.01-0.08％，Ni：0.50-1.30％，Nb：0.01-0.06％，V：0.03-0.12％，Al：0.01-0.05％，Ca：0.0005-0.005% also meets following relational expression: 5 < Ni/ (C*Mo)≤50 simultaneously, and surplus isFe and other inevitable impurity.
2. 890MPa grade high-strength steel as claimed in claim 1, is characterized in that, its microstructure is backFire sorbite.
3. 890MPa grade high-strength steel as claimed in claim 1, is characterized in that, its carbon equivalent Ceq=C+Mn/6+(Cr+Mo+V)/5+Ni/15≤0.65。
4. 890MPa grade high-strength steel as claimed in claim 1, is characterized in that, its yield strength is greater thanThe low-temperature impact toughness that 890MPa, tensile strength are greater than at 960MPa ,-40 DEG C is greater than 100J.
5. a steel pipe, it adopts the 890MPa grade high-strength steel as described in any one in claim 1-4Make.
6. the manufacture method of steel pipe as claimed in claim 5, is characterized in that, comprises step:
(1) make steel and be cast into round base;
(2) justify base heating;
(3) high-pressure water descaling;
(4) tube rolling, rolls rear air cooling;
(5) modified heat treatment: hardening heat is 880-930 DEG C, temperature retention time is 30-60min,Then shrend. Carry out high tempering at 580-650 DEG C, temperature retention time is 30-80min;
(6) high-pressure water descaling;
(7) thermal straightening: the control of thermal straightening temperature is 500-600 DEG C.
7. the manufacture method of steel pipe as claimed in claim 6, is characterized in that, also comprises step (8) welderingConnect: adopt gas shielded arc welding by welding after some sections of steel pipe docking, welding wire deposited metal tension is strongDegree is not less than 960MPa, preheat temperature 90-150 DEG C.
8. the manufacture method of the steel pipe as described in claim 6 or 7, is characterized in that, in described step (2)In, control firing rate 9-11min/cm, soaking temperature is 1220-1240 DEG C and insulation60-120min。
9. the manufacture method of the steel pipe as described in claim 6 or 7, is characterized in that, in described step (3)In, control water under high pressure pressure and be greater than 10MPa.
10. the manufacture method of the steel pipe as described in claim 6 or 7, is characterized in that, in described step (4)In, controlling finish to gauge rolling temperature is 950-1050 DEG C.
The manufacture method of 11. steel pipes as described in claim 6 or 7, is characterized in that, in described step (6)In, control water under high pressure pressure and be greater than 6MPa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610105103.3A CN105586529B (en) | 2016-02-25 | 2016-02-25 | A kind of 890MPa grade high-strengths steel, steel pipe and its manufacture method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610105103.3A CN105586529B (en) | 2016-02-25 | 2016-02-25 | A kind of 890MPa grade high-strengths steel, steel pipe and its manufacture method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105586529A true CN105586529A (en) | 2016-05-18 |
| CN105586529B CN105586529B (en) | 2017-10-31 |
Family
ID=55926425
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610105103.3A Active CN105586529B (en) | 2016-02-25 | 2016-02-25 | A kind of 890MPa grade high-strengths steel, steel pipe and its manufacture method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105586529B (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2019179354A1 (en) * | 2018-03-21 | 2019-09-26 | 宝山钢铁股份有限公司 | Low temperature resistant oil casing with high strength and high toughness, and manufacturing method thereof |
| CN110317994A (en) * | 2018-03-30 | 2019-10-11 | 宝山钢铁股份有限公司 | A kind of high heat input welding unimach and its manufacturing method |
| CN111748727A (en) * | 2019-03-27 | 2020-10-09 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN112553526A (en) * | 2020-11-20 | 2021-03-26 | 林州凤宝管业有限公司 | 960 MPa-level ultrahigh-strength structural steel, steel pipe and manufacturing method and application thereof |
| CN113106347A (en) * | 2021-04-13 | 2021-07-13 | 无锡恒丰祥钢管科技有限公司 | High-temperature-resistant seamless steel tube and preparation method thereof |
| CN114892085A (en) * | 2022-05-06 | 2022-08-12 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001011568A (en) * | 1999-06-23 | 2001-01-16 | Sumitomo Metal Ind Ltd | Steel for inline heat treatment and production of seamless steel pipe composed of this steel and excellent in sulfide stress corrosion cracking resistance |
| JP2003160811A (en) * | 2001-11-26 | 2003-06-06 | Nippon Steel Corp | Method for manufacturing tempered high-tensile- strength steel sheet superior in toughness |
| CN101629476A (en) * | 2009-08-05 | 2010-01-20 | 天津钢管集团股份有限公司 | High strength and high toughness petroleum casing pipe capable of bearing low temperature within -40 to -80 |
| CN102459677A (en) * | 2009-06-24 | 2012-05-16 | 杰富意钢铁株式会社 | High-strength seamless steel tube for use in oil wells, which has excellent resistance to sulfide stress cracking and production method for same |
| JP2013104124A (en) * | 2011-11-16 | 2013-05-30 | Jfe Steel Corp | Directly quenched and tempered high tensile strength steel sheet having excellent bendability and method for producing the same |
| CN104862613A (en) * | 2015-05-26 | 2015-08-26 | 宝山钢铁股份有限公司 | High-strength steel, high-strength steel pipe and manufacturing method of high-strength steel pipe |
-
2016
- 2016-02-25 CN CN201610105103.3A patent/CN105586529B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001011568A (en) * | 1999-06-23 | 2001-01-16 | Sumitomo Metal Ind Ltd | Steel for inline heat treatment and production of seamless steel pipe composed of this steel and excellent in sulfide stress corrosion cracking resistance |
| JP2003160811A (en) * | 2001-11-26 | 2003-06-06 | Nippon Steel Corp | Method for manufacturing tempered high-tensile- strength steel sheet superior in toughness |
| CN102459677A (en) * | 2009-06-24 | 2012-05-16 | 杰富意钢铁株式会社 | High-strength seamless steel tube for use in oil wells, which has excellent resistance to sulfide stress cracking and production method for same |
| CN101629476A (en) * | 2009-08-05 | 2010-01-20 | 天津钢管集团股份有限公司 | High strength and high toughness petroleum casing pipe capable of bearing low temperature within -40 to -80 |
| JP2013104124A (en) * | 2011-11-16 | 2013-05-30 | Jfe Steel Corp | Directly quenched and tempered high tensile strength steel sheet having excellent bendability and method for producing the same |
| CN104862613A (en) * | 2015-05-26 | 2015-08-26 | 宝山钢铁股份有限公司 | High-strength steel, high-strength steel pipe and manufacturing method of high-strength steel pipe |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2019179354A1 (en) * | 2018-03-21 | 2019-09-26 | 宝山钢铁股份有限公司 | Low temperature resistant oil casing with high strength and high toughness, and manufacturing method thereof |
| RU2751629C1 (en) * | 2018-03-21 | 2021-07-15 | Баошань Айрон Энд Стил Ко., Лтд. | Low temperature resistant oil casing pipe with high strength and high viscosity, as well as method for its manufacture |
| US11519049B2 (en) | 2018-03-21 | 2022-12-06 | Baoshan Iron & Steel Co., Ltd. | Low temperature resistant oil casing having high strength and high toughness, and manufacturing method thereof |
| CN110317994A (en) * | 2018-03-30 | 2019-10-11 | 宝山钢铁股份有限公司 | A kind of high heat input welding unimach and its manufacturing method |
| CN110317994B (en) * | 2018-03-30 | 2021-12-17 | 宝山钢铁股份有限公司 | Ultrahigh-strength steel for high heat input welding and manufacturing method thereof |
| CN111748727A (en) * | 2019-03-27 | 2020-10-09 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN111748727B (en) * | 2019-03-27 | 2022-01-14 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN112553526A (en) * | 2020-11-20 | 2021-03-26 | 林州凤宝管业有限公司 | 960 MPa-level ultrahigh-strength structural steel, steel pipe and manufacturing method and application thereof |
| CN112553526B (en) * | 2020-11-20 | 2022-04-22 | 林州凤宝管业有限公司 | 960 MPa-level ultrahigh-strength structural steel, steel pipe and manufacturing method and application thereof |
| CN113106347A (en) * | 2021-04-13 | 2021-07-13 | 无锡恒丰祥钢管科技有限公司 | High-temperature-resistant seamless steel tube and preparation method thereof |
| CN114892085A (en) * | 2022-05-06 | 2022-08-12 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
| CN114892085B (en) * | 2022-05-06 | 2023-03-03 | 鞍钢股份有限公司 | Wide and thick steel plate for advanced nuclear power unit positioning and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105586529B (en) | 2017-10-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP2218801B1 (en) | Steel plate with yield strength of 800mpa grade and low weld cracking sensitivity, and manufacture method thereof | |
| CN101215669B (en) | High-strength thick steel plate for large-scale petroleum storing tank and low-cost manufacturing method thereof | |
| CN114959460B (en) | Low-yield-ratio easy-welding weather-resistant bridge steel and manufacturing method thereof | |
| CN103352167B (en) | A kind of low yield strength ratio high strength bridge steel plate and manufacture method thereof | |
| CN101397626B (en) | High intensity and high-toughness hot-rolled steel sheet and method for producing the same | |
| WO2016095721A1 (en) | Quenched-tempered high-strength steel with yield strength of 900 mpa to 1000 mpa grade, and manufacturing method therefor | |
| CN105586529A (en) | 890MPa-level high-strength steel, steel pipe and manufacturing method of steel pipe | |
| CN100396809C (en) | Thick steel plate with great line energy and low welding crack sensitivity and its production process | |
| CN101906575B (en) | High-strength economical X70 pipeline steel hot-rolling flat plate and production method thereof | |
| CN101161847B (en) | High-ductility steel for hot-bending bends and production method for hot rolled plates thereof | |
| CN104328356A (en) | Manufacturing method of thin-specification high-strength-structure steel plate with steckel mill | |
| CN110656288B (en) | Steel for ultra-wide, ultra-thick and high-toughness X80 straight welded pipe and production method thereof | |
| CN101619423A (en) | Steel plate for high-strength high-toughness low-yield easily-welding structure and method for manufacturing same | |
| CN109402500A (en) | The hot-bending bends of low-temperature good toughness X80 Wide and Heavy Plates and its production method | |
| CN109207849B (en) | High-strength high-plasticity 1000 MPa-grade hot rolled steel plate and preparation method thereof | |
| CN109504897A (en) | A kind of big thickness water power steel of 80kg grades of low-carbon-equivalent low-crackle sensitive and its manufacturing method | |
| CN107747068B (en) | A kind of heat-resistance stainless steel seamless pipe and preparation method thereof | |
| JP4071906B2 (en) | Manufacturing method of steel pipe for high tension line pipe with excellent low temperature toughness | |
| CN108456827A (en) | A kind of modified adds vanadium chrome molybdenum steel plate and its production method | |
| CN102796967A (en) | 800 MPa economic corrosion-resistance and high-strength steel plate | |
| CN105624585B (en) | A kind of floating LNG pipelines X80Q hot-rolled thick planks and its production method | |
| CN102691018A (en) | Low-compression ratio super-strength steel plate for ocean engineering and manufacturing method thereof | |
| WO2014114111A1 (en) | 500mpa longitudinally-welded steel tube having low yield ratio and producing method therefor | |
| CN103695807B (en) | Strong X100 Pipeline Steel Plate of superelevation that crack arrest is excellent and preparation method thereof | |
| CN107988548B (en) | A kind of X80 Pipeline Steel Plate and its production method adapting to low temperature Naked dew environment |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |