CN102230133B - Cr-containing Alloy steel and manufacturing method thereof - Google Patents
Cr-containing Alloy steel and manufacturing method thereof Download PDFInfo
- Publication number
- CN102230133B CN102230133B CN201110154407.6A CN201110154407A CN102230133B CN 102230133 B CN102230133 B CN 102230133B CN 201110154407 A CN201110154407 A CN 201110154407A CN 102230133 B CN102230133 B CN 102230133B
- Authority
- CN
- China
- Prior art keywords
- steel
- temperature
- steel alloy
- rolling
- steel billet
- 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.)
- Expired - Fee Related
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to Cr-containing alloy steel and a manufacturing method thereof. The Cr-containing alloy steel contains 0.03-0.07 % of C, 1.50-4.99 % of Cr, 0.03-0.05 % of Nb, 0.15-0.25 % of Mo, 0.01-0.03 % of Ti and the balance of Fe and inevitable impurities in percentage by weight. The Cr-containing alloy steel provided by the invention has the advantages of good welding property and corrosion resistance, in particular good resistance to carbon dioxide local corrosion, and low production cost, and can be used for manufacturing oil gas transmission lines.
Description
Technical field
The present invention relates to a kind of resistant to carbon dioxide local corrosion containing Cr steel alloy and manufacture method thereof, particularly under oil-gas field carbonated environment, there is not local corrosion and have weldability containing Cr steel alloy, this steel alloy can be used for manufacturing oil gas pipeline.
Background technology
Usually association carbonic acid gas in oil reservoir and gas reservoir, carbonic acid gas is water-soluble, forms carbonic acid, can cause heavy corrosion to oil gas pipeline.Humid carbon dioxide usually can cause carbon steel pipe line generation local corrosion and bore a hole, if adopt stainless steel, although can solve etching problem, cost significantly improves, and stainless steel exists the problem of weldability difference.Therefore, exploitation can resistant to carbon dioxide local corrosion, to have weldability, cost new steel grade cheaper again concurrently very necessary.
The low alloy steel of Chinese invention patent application 01126575.2(carbon dioxide corrosion-resistant and tubing and casing) disclose a kind of steel alloy, its chemical composition is: C:0.01-0.3%, Si:0.10-1.0%, Mn; 0.1-2.0%, Cr:0.5-5.0%, Mo:0.01-1.0%, Cu:0.05-2.0%, Ni:0.05-1.0%, Al:0.005-0.1%, all the other are Fe and inevitable impurity.This patent is the Cr element (0.5-5.0%) by adding a wider range, suppress the corrosion under the combination of acidic corrosion working conditions such as wetting carbonic acid gas, chlorion, hydrogen sulfide, this patent for the manufacture of Oil/gas Well tubing and casing, the finished product be organized as sorbite tissue.
Chinese invention patent application 200910117129.x(mono-kind is containing Cr thick-wall pipeline steel and coiled sheet controlled rolling and controlled cooling method thereof) disclose a kind of steel alloy, its chemical composition: Cr:0.20-0.90%, C:0.0,3-0.09%, Si:0.20-0.35%, Mn; 1.00-1.30%, Ti:0.010-0.030%, Nb:0.03-0.08%, Cu:0.15-0.30%, Ni:0.10-0.40%, this invention is mainly through adding a small amount of Cr(0.20-0.90%) improve intensity and crystal grain thinning, form many and thin acicular ferrite structure.
When conveying high-pressure, carbonated oil gas medium, easily there is local corrosion and cause pipeline leakage in carbon steel pipe line, if but by adding a large amount of alloying element to gain in strength and anti-local corrosion performance, one is roll up cost, and two is possible cause deteriorated weldability.Therefore, study on a kind of basis having excellent weldability concurrently and necessitated by the anti-local corrosion steel alloy of suitable component and explained hereafter.
Summary of the invention
The invention provides a kind of containing Cr steel alloy and manufacture method thereof.
In first aspect, the invention provides a kind of containing Cr steel alloy, it contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
In second aspect, the invention provides its making containing Cr steel alloy by first aspect present invention.
In the third aspect, the invention provides the method manufactured containing Cr steel alloy, comprise the steps:
(1) provide the steel billet containing Cr steel alloy, described steel billet contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
(2) forge described steel billet, wherein final forging temperature is not less than 1000 DEG C;
(3) steel billet through forging is made to carry out following two-phase control rolling,
A () first stage is rough rolling step, wherein the start rolling temperature of rough rolling step is 1100-1150 DEG C, is preferably 1100-1130 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C, is preferably 1000 DEG C;
B () subordinate phase is the finish rolling stage, wherein the start rolling temperature in finish rolling stage is 900-950 DEG C, is preferably 930-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C, is preferably 880-900 DEG C;
The draft of wherein said rough rolling step is greater than 45%, and whole operation of rolling total reduction is not less than 65%;
(4) steel through rolling is cooled, obtain described steel alloy, wherein final cooling temperature is 500-600 DEG C, and be preferably 540-580 DEG C, speed of cooling is 10-35 DEG C/s.
Specifically, the application comprises following embodiment:
Embodiment 1. 1 kinds is containing Cr steel alloy, and it contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
2. embodiment 1 containing Cr steel alloy, wherein, contain
C：0.03-0.04%，
Cr：2.00-2.99%，
Nb：0.03-0.05%，
Mo：0.20-0.25%，
Ti:0.02-0.03%, is all weight percentage above.
3. embodiment 1 containing Cr steel alloy, wherein, contain
C：0.03-0.035%，
Cr：3.01-4.99%，
Nb：0.03-0.05%，
Mo：0.20-0.25%，
Ti:0.02-0.03%, is all weight percentage above.
4. any one of embodiment 1-3 containing Cr steel alloy, wherein, the Si also containing 0.15-0.25wt%.
5. any one of embodiment 1-3 containing Cr steel alloy, wherein, the Si also containing 0.15-0.20wt%.
6. any one of embodiment 1-5 containing Cr steel alloy, wherein, the Mn also containing 0.40-0.60wt%.
7. any one of embodiment 1-5 containing Cr steel alloy, wherein, the Mn also containing 0.40-0.50wt%.
8. any one of embodiment 1-7 containing Cr steel alloy, wherein said steel alloy has bainite structure.
9. an oil gas pipeline, its making containing Cr steel alloy any one of embodiment 1-8.
10. manufacture the method containing Cr steel alloy, comprise the steps:
(1) provide the steel billet containing Cr steel alloy, described steel billet contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
(2) forge described steel billet, wherein final forging temperature is not less than 1000 DEG C;
(3) steel billet through forging is made to carry out following two-phase control rolling,
A () first stage is rough rolling step, wherein the start rolling temperature of rough rolling step is 1100-1150 DEG C, is preferably 1100-1130 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C, is preferably 1000 DEG C;
B () subordinate phase is the finish rolling stage, wherein the start rolling temperature in finish rolling stage is 900-950 DEG C, is preferably 930-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C, is preferably 880-900 DEG C;
The draft of wherein said rough rolling step is greater than 45%, and whole operation of rolling total reduction is not less than 65%;
(4) steel through rolling is cooled, obtain described steel alloy, wherein final cooling temperature is 500-600 DEG C, preferred 540-580 DEG C, and speed of cooling is 10-35 DEG C/s.
The method of 11. embodiments 10, when wherein forging described steel billet, first by after described heating steel billet to 1150-1200 DEG C, preferably 1180-1200 DEG C also insulation, then carries out described forging.
The method of 12. embodiments 10 or 11, wherein the draft of rough rolling step is greater than 50%.
13. the method any one of embodiment 10-12, wherein said steel billet contains
C：0.03-0.04%，
Cr：2.00-2.99%，
Nb：0.03-0.05%，
Mo：0.20-0.25%，
Ti:0.02-0.03%, is all weight percentage above.
Method any one of 14. embodiment 10-12, wherein, described steel billet contains
C：0.03-0.035%，
Cr：3.01-4.99%，
Nb：0.03-0.05%，
Mo：0.20-0.25%，
Ti:0.02-0.03%, is all weight percentage above.
Method any one of 15. embodiment 10-14, wherein, the Si of described steel billet also containing 0.15-0.25wt%.
Method any one of 16. embodiment 10-14, wherein, the Si of described steel billet also containing 0.15-0.20wt%.
Method any one of 17. embodiment 10-16, wherein, the Mn of described steel billet also containing 0.40-0.60wt%.
Method any one of 18. embodiment 10-16, wherein, the Mn of described steel billet also containing 0.40-0.50wt%.
Method any one of 19. embodiment 10-17, wherein, described steel alloy has bainite structure.
Embodiment
Hereinafter, steel alloy of the present invention will more be described in detail based on the reason of the operation of alloy compositions and the numerical limits of alloy compositions according to the embodiment of the present invention.Unless otherwise noted, otherwise " % " in this specification sheets refers to mass percent.
The first aspect of the application
A first aspect of the present invention relates to a kind of containing Cr steel alloy, and it contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
Hereinafter, the present invention is described in detail by according to the reason of the operation of often kind of component and the numerical limits of each component.
c (carbon): 0.03-0.07%
C can affect obdurability, the weldability of steel alloy.C content is too high, and weldability can worsen, degraded toughness.C content also should not require too low, otherwise smelting technology is not too economical.Therefore, in a first aspect of the present invention, C content controls at 0.03-0.07%.In one embodiment, C content can be 0.03-0.04%.In another embodiment, C content can be 0.03-0.035%.
cr (chromium): 1.50-4.99%
Inventor finds, has good resistant to carbon dioxide local corrosion performance containing Cr steel alloy.Particularly Cr content is the steel alloy of 1.50-4.99%, even if under high-pressure carbon dioxide environment, still has good resistant to carbon dioxide local corrosion performance.In the corrosion test of this steel alloy under high-pressure carbon dioxide environment, this steel alloy can form the special corrosion products film of one deck.Carry out research to the characteristic of corrosion products film to show, in this layer of corrosion products film, there is significant enrichment in Cr, the density of film and protectiveness strengthened greatly, plays the effect of half passive film, prevent the generation of local corrosion.Particularly when Cr content is more than 3%, in corrosion products film, the enrichment degree of Cr improves greatly, and film becomes fine and close, protectiveness improves, and average corrosion rate significantly reduces.But when Cr content is more than 5%, the weld hardness of steel is comparatively large, still can not meet the requirement of DNV standard.Therefore, in the first aspect of the application, Cr content is 1.50-4.99%.In one embodiment, Cr content can be 2.00-2.99%.In another embodiment, Cr content can be 3.01-4.99%.
nb (niobium): 0.03-0.05%
The steel alloy of the application's first aspect contains Nb element.Nb element can crystal grain thinning, reduces superheated susceptivity and the temper brittleness of steel, improves its intensity; Meanwhile, Nb can improve the ability of resistant to hydrogen under the weather-resistant of steel and high temperature, nitrogen, ammonia corrosion; Nb also can improve the welding property of steel.But too much Nb can reduce plasticity and the toughness of steel.Therefore, in the application's first aspect, Nb content controls as 0.03-0.05%.
mo (molybdenum): 0.15-0.25%
The steel alloy of the application's first aspect contains Mo element.Mo, as the alloy element of steel, can improve the intensity of steel, particularly hot strength and toughness; Improve the corrosion stability of steel in acid-base solution and liquid metal; Improve the wear resistance of steel and improve hardening capacity, weldability and thermotolerance.Mo adds into improve corrosion resisting property, particularly anti-local corrosion performance on the one hand, if but Mo too high levels (>1%), processing characteristics and plasticity can be made to worsen.Therefore, in the first aspect of the application, Mo content is 0.15-0.25%.In one embodiment, Mo content can be 0.20-0.25%.
ti (titanium): 0.01-0.03%,
The steel alloy of the application's first aspect contains Ti element.Ti is strong reductor in steel, and it can make the dense internal organization of steel, crystal grain thinning power; Reduce aging sensitivity and cold shortness, improving welding property.In the first aspect of the application, Ti content is 0.01-0.03%, thus recrystallization temperature and the AUSTENITE GRAIN COARSENING temperature of steel can be improved, thus control the grain-size in continuous casting and heat-processed, play crystal grain thinning, the yield strength improving steel and toughness effect.In one embodiment, Ti content can be 0.02-0.03%.
si (silicon): 0.15-0.25%
mn (manganese): 0.40-0.60%.
The steel alloy of the application's first aspect can also contain Si and/or Mn further, to obtain the steel alloy of the present invention in erosion resistance, welding property and mechanical strength etc. with optimization synthesis performance further.
In one embodiment, Si content can be 0.15-0.25%.In another embodiment, Si content can be 0.15-0.20%.
In one embodiment, Mn content can be 0.40-0.60%.In another embodiment, Mn content can be 0.40-0.50%.
For the application's first aspect containing Cr steel alloy, for impurity elements such as S, P, O wherein, ensure that it is in certain controlled range as far as possible, in case its too high levels causes steel to have other bad performances.In one embodiment, S content is less than 0.006%.In another embodiment, P content is less than 0.012%.In an embodiment again, O content is less than 0.002%.
In one embodiment, should contain containing Cr steel alloy:
C：0.03-0.07%，Si：0.15-0.25%，
Mn；0.40-0.60%，Cr：1.50-4.99%，
Nb：0.03-0.05%，Mo：0.15-0.25%，
Ti：0.01-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
In one embodiment, should contain containing Cr steel alloy:
C：0.03-0.04%，Si：0.15-0.25%，
Mn；0.40-0.60%，Cr：2.00-2.99%，
Nb：0.03-0.05%，Mo：0.20-0.25%，
Ti：0.02-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
In one embodiment, should contain containing Cr steel alloy:
C：0.03-0.35%，Si：0.15-0.20%，
Mn；0.40-0.50%，Cr：3.01-4.99%，
Nb：0.03-0.05%，Mo：0.20-0.25%，
Ti：0.02-0.03%，
All the other are Fe and inevitable impurity, are all weight percentage above.
The Cr steel alloy that contains of the application's first aspect has bainite structure.In one embodiment, containing in Cr steel alloy in the application's first aspect, bainite structure can account for the majority of total alloy phase of described steel alloy, and such as, bainite structure can account for more than 50% of total alloy phase of described steel alloy.In another embodiment, bainite structure can account for the 60-90% of total alloy phase of described steel alloy, such as 80-90%.In another embodiment, the described Cr steel alloy that contains mainly comprises bainite structure and ferritic structure, and wherein bainite structure can account for more than 50%, such as, can account for 60-90%, as 70-90%.
The steel alloy of the application has good welding property and corrosion resistance nature, particularly good resistant to carbon dioxide local corrosion performance, and production cost is low, can be used in as conveying high-pressure, carbonated oil gas medium pipe line steel.The Cr steel alloy tool compared with existing X60-X70 pipe line steel that contains of the present invention has the following advantages:
1., under oil-gas transportation environment, average corrosion rate reduces 3-4 doubly
2., under high-pressure carbon dioxide oil-gas transportation environment, there is not local corrosion.
The Cr steel alloy tool compared with existing austenitic stainless steel 316 L that contains of the present invention has the following advantages:
1. cost reduces 3-5 doubly
2. high, the problem that there is not weld cracking of good weldability, welding efficiency.
the second aspect of the application
The second aspect of the application relates to a kind of oil gas pipeline, and it can making containing Cr steel alloy by the application's first aspect.
The Cr steel alloy that contains described by each embodiment of the application's first aspect is all applicable to the application's second aspect.
In the application's second aspect, this oil gas pipeline can use preparing containing Cr steel alloy of the application's first aspect according to technology known in the art.Because the Cr steel alloy that contains of the application's first aspect has good welding property and corrosion resistance nature, particularly good resistant to carbon dioxide local corrosion performance, thus, the oil gas pipeline of the application's second aspect equally also has good resistant to carbon dioxide local corrosion performance and welding property, can be used in conveying high-pressure, carbonated oil gas medium.
the third aspect of the application
The application's third aspect relates to the method manufactured containing Cr steel alloy.The method comprises the steps:
(1) provide the steel billet containing Cr steel alloy, described steel billet contains
C:0.03-0.07%，
Cr:1.50-4.99%，
Nb:0.03-0.05%，
Mo:0.15-0.25%，
Ti:0.01-0.03%，
(2) forge described steel billet, wherein final forging temperature is not less than 1000 DEG C;
(3) steel billet through forging is made to carry out following two-phase control rolling,
A () first stage is rough rolling step, wherein the start rolling temperature of rough rolling step is 1100-1150 DEG C, is preferably 1100-1130 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C, is preferably 1000 DEG C;
B () subordinate phase is the finish rolling stage, wherein the start rolling temperature in finish rolling stage is 900-950 DEG C, is preferably 930-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C, is preferably 880-900 DEG C;
The draft of wherein said rough rolling step is greater than 45%, and whole operation of rolling total reduction is not less than 65%;
(4) steel through rolling is cooled, obtain described steel alloy, wherein final cooling temperature is 500-600 DEG C, and be preferably 540-580 DEG C, speed of cooling is 10-35 DEG C/s.
Above-mentioned each preparation process is below described respectively.
(1) steel billet is provided
Steel billet is provided to carry out as follows: first according to the design mix of the application's steel alloy, after starting material needed for accurate calculation, to smelt; Then, teeming, air cooling steel ingot, to room temperature, namely obtains required steel billet.In smelting process, steel sample can be gathered, carry out composition analysis, to guarantee the design requirements meeting steel.
The smelting of steel can adopt technology known in the art to carry out, such as, carry out in vacuum smelting furnace.In one embodiment, in smelting process, Al can be utilized to carry out deoxidation treatment.In addition, can ensure to carry out solution treatment at about 1600 DEG C temperature, its main purpose wishes to improve plasticity and the toughness of steel or alloy, for precipitation hardening process is got ready.
(2) forge
Steel billet is after casting, and for obtaining excellent over-all properties, general needs forges.In forging process, final forging temperature is not less than 1000 DEG C usually, to obtain the steel alloy of the present invention in erosion resistance, welding property and mechanical strength etc. with optimization synthesis performance.
In one embodiment, can forge as follows:
Described heating steel billet is incubated for some time (such as 0.5-5 hour, such as 1-2 hour) to 1150-1200 DEG C, preferably 1180-1200 DEG C, comes out of the stove and namely forge; Final forging temperature ensures to be not less than 1000 DEG C.Other controls of forging process can be carried out according to mode known in the art.
(3) rolling
In order to obtain the steel of excellent property, general needs is rolled the steel billet through forging.In the application's third aspect, rolling technology adopts hot rolling technology usually.
In one embodiment, rolling technology is two-phase control rolling technique, wherein
A () first stage is rough rolling step, wherein the start rolling temperature of rough rolling step is 1100-1150 DEG C, is preferably 1100-1130 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C, is preferably 1000 DEG C;
B () subordinate phase is the finish rolling stage, wherein the start rolling temperature in finish rolling stage is 900-950 DEG C, is preferably 930-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C, is preferably 880-900 DEG C;
The draft of wherein said rough rolling step is greater than 50%, and whole operation of rolling total reduction is not less than 65%.
The roughing of first stage is the roughing of austenite recrystallization district.In one embodiment, the start rolling temperature of rough rolling step is 1100-1150 DEG C, is preferably 1100-1130 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C, is preferably about 1000 DEG C.In one embodiment, for the roughing of this first stage, total reduction can be greater than 50%.In another embodiment, the roughing of this first stage can carry out multiple passage, and such as 2-4 passage, each pass deformation can be greater than 15% ~ 20%.
The finish rolling of subordinate phase is austenite non-recrystallization zone finish rolling.The finish rolling stage carries out at austenite Unhydrated cement, and austenite crystal can be made fully to flatten, and forms slip band at intra-die.In one embodiment, the start rolling temperature in finish rolling stage is 900-950 DEG C, is preferably 930-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C, is preferably 880-900 DEG C.In one embodiment, for this finish rolling stage, draft can be 60%.In another embodiment, this finish rolling stage can carry out multiple passage, such as 2-5 passage.
(4) controlled cooling model
Controlled cooling model is carried out to steel after bundle, thus obtains the steel alloy of the application.What control to roll rear steel opens cold temperature, speed of cooling and final cooling temperature, can reach control phase-change type, crystal grain thinning and control the objects such as precipitation, can improve the character such as the intensity of steel and toughness.
Final cooling temperature is the temperature that steel stops cooling when carrying out rolling rear controlled cooling model.In fact controlled cooling model is exactly the phase transition process controlling steel, to obtain the structure of steel performance required.Therefore, final cooling temperature is the epochmaking processing parameter of Controlled cooling process.In a kind of embodiment of the application, final cooling temperature is 500-600 DEG C, preferred 540-580 DEG C.
Rate of cooling also can affect the phase constitution of the application's steel alloy.In a kind of embodiment of the application, speed of cooling is 10 ~ 35 DEG C/s, particularly 10-30 DEG C/s.
For this Controlled cooling process, those skilled in the art can select the suitable type of cooling and heat-eliminating medium to carry out.Such as, in one embodiment, Water-Curta in Cooling mode can be adopted.In another embodiment, air cooling mode can be adopted.
After controlled cooling model step, in a conventional manner steel alloy can be further cooled to room temperature as required.
As mentioned above, adopt the method for the application's third aspect, the steel alloy with bainite structure can be obtained, the excellent combination properties such as its corrosion resisting property, welding property and mechanical property.In one embodiment, what obtain in the application's third aspect contains in Cr steel alloy, and bainite structure can account for the great majority of total alloy phase of described steel alloy, obtains mainly containing the steel alloy of bainite structure.Such as, in one embodiment, bainite structure can account for more than 50% of total alloy phase of described steel alloy.In another embodiment, bainite structure can account for the 60-90% of total alloy phase of described steel alloy, such as 80-90%.In another embodiment, the described Cr steel alloy that contains can mainly comprise bainite structure and ferritic structure, and wherein bainite structure can account for more than 50%, such as, can account for 60-90%, as 70-90%.
Below provide a concrete manufacturing processed of the application's steel alloy:
(1) vacuum metling is carried out according to design mix, teeming according to the method for this area;
(2) steel ingot is heated to 1200C with stove, comes out of the stove and namely forge after insulation 1h; Final forging temperature ensures to be not less than 1000C;
(3) be rolled
1. the first stage is rough rolling step, and ensure that start rolling temperature is at 1100 DEG C, finishing temperature is at about 1000 DEG C; Also to ensure that the total reduction of steel ingot is greater than 50%.Such as, treat that temperature thickness is 32-38mm, through 2 passes, concrete thickness parameter is changed to: 70mm – 48mm – 34mm;
2. subordinate phase is the finish rolling stage, and ensure that start rolling temperature is at about 930 DEG C, finishing temperature control is at about 880 DEG C.Such as, for rolling into target size, 3 passages can be divided to carry out, and concrete thickness parameter is: 34mm – 24mm – 16mm – 12mm(3 passage);
(4) after, carry out controlled cooling model, when Controlled cooling process starts, temperature controls at about 860 DEG C, and final cooling temperature controls at 540 DEG C ~ 580 DEG C, and speed of cooling is 10-35 DEG C/s.
Thus, can namely be obtained this containing Cr steel alloy.
As previously mentioned, the steel alloy adopting the method for the application's third aspect to prepare has the over-all properties of excellence in corrosion resisting property, welding property and mechanical property etc., particularly there is good resistant to carbon dioxide local corrosion performance and welding property, and production cost is low, can be used in as conveying high-pressure, carbonated oil gas medium pipe line steel, manufacture oil gas pipeline.
Embodiment
According to the chemical constitution listed by table 1, after smelting, forging, rolling, thermal treatment, obtain each steel A1-A6 of the present invention, and contrast steel B1-B3.
Wherein, steel A1-A6 of the present invention carry out forging according to following process, rolling and thermal treatment:
(1) smelt according to the chemical constitution listed by table 1, smelting gained steel ingot is heated to 1200C with stove, come out of the stove and namely forge after this temperature 1h, final forging temperature ensures to be not less than 1000C.
(2) steel billet after rolling forging
A () carries out the rough rolling step of first stage, ensure that start rolling temperature is at 1100 DEG C, finishing temperature is at about 1000 DEG C; The total reduction of steel ingot is greater than 50%;
B () subordinate phase is the finish rolling stage, ensure that start rolling temperature is at about 930 DEG C, finishing temperature control is at about 880 DEG C;
(3) after steel plate rolling becomes target size, cool, when beginning to cool down, temperature controls at about 860 DEG C, and final cooling temperature controls, at 540 DEG C ~ 580 DEG C, to control speed of cooling at 10-35 DEG C/s.Particularly, the speed of cooling that steel A1 of the present invention adopts is 15 DEG C/s, and the speed of cooling that steel A4 of the present invention adopts is 30 DEG C/s, and the speed of cooling that steel A6 of the present invention adopts is 35 DEG C/s.
According to the composition of contrast steel B1-B3, adopt conventional smelting, forging, rolling technology, adopt the speed of cooling of 7 DEG C/s, obtain the sample of compared steel B1-B3, it is organized as sorbite.
Table 1 is steel of the present invention and the chemical composition and the tissue that contrast steel, and wherein A1-A6 is steel of the present invention, and B1-B3 is contrast steel.
Table 1: the chemical composition (wt, %) (remaining as Fe) of test steel
Optical microstructure's photo of steel A1, A4 and A6 of the present invention respectively as Fig. 1 a), Fig. 1 b) and Fig. 1 c) shown in.From the light micrograph shown in this figure, steel A1, A4 and A6 of the present invention all have bainite structure, and wherein the ratio of the bainite structure of three kinds of steel sees the following form 2.Particularly, in steel A4 and A6 of the present invention, bainite structure occupies the majority, and reaches 70% and 80% respectively.
Table 2: the ratio measuring result of bainite structure
| Ferrite | Perlite | Bainite | |
| Steel A1 of the present invention | 80% | 10% | 10% |
| Steel A4 of the present invention | 30% | 70% | |
| Steel A6 of the present invention | 20% | 80% |
Intensity, unit elongation, the hardness value of steel of the present invention and contrast steel, and characterize the impelling strength of welding property quality and weld decay speed in table 3.As shown in Table 3, the tensile strength of steel of the present invention etc. a little less than contrast steel, but also meet application requiring.And importantly, the impelling strength (evaluating the key factor of weldability quality) of contrast steel is obviously low than the present invention steel, this illustrates that the welding property of contrast steel is obviously poor than the present invention steel.Another important factor of evaluation is the erosion rate of welding joint.As shown in Table 3, the erosion rate of steel of the present invention is all starkly lower than contrast steel, and this shows that steel of the present invention has the corrosion resistance nature being obviously better than contrasting steel; Particularly, steel A4 of the present invention has minimum erosion rate, and corrosion resistance nature is best.
Table 3: test steel welded joint mechanical property and corrosive nature
Test experiments and the condition of each index listed in table 3 are as follows:
1. erosion rate
Test name: High Temperature High Pressure CO
2corrosion simulated experiment
Specimen size: the 1/8 circular arc sample of external diameter Φ 72mm, internal diameter Φ 64mm
Testing installation: volume is the High Temperature High Pressure FCZ magnetic force driving reactor of 3L
Experimental temperature: 80 DEG C
CO
2dividing potential drop: 1.0MPa
Experimental period: 168h
Flow velocity: 1m/s
Experimental solutions medium: simulation oil field Produced Liquid, utilize deionized water and analytical reagent to prepare, chemical composition is as shown in table 4, before experiment, pass into N
2deoxygenation, continues in experimentation to pass into CO
2solution is reached capacity.
The ionic concn of table 4 experimental solutions medium
2. mechanical property
Mechanical property is carried out according to following standard:
GB 2649-89 " welding joint mechanical property sample sampling method "
GB 2650-89 " welding joint impact test method ": Charpy V test is carried out on JB-300B shock-testing machine.Specimen size: 55 × 10 × 5mm. welding joint impact experiment temperature is-30 DEG C
GB 2651-89 " welding joint stretching test method ": be of a size of 120 × 18 × 3mm sheet specimens, weld seam is positioned at sample center, and MTS810 tensile testing machine carries out tension test.
Accompanying drawing explanation
Fig. 1 is optical microstructure's photo of steel A1, A4 and A6 of the present invention, wherein respectively as Fig. 1 a), Fig. 1 b) and Fig. 1 c) be respectively the photo of steel A1, A4 and A6 of the present invention.
Claims (21)
1., containing a Cr steel alloy, it consists of:
C： 0.03-0.07％，
Cr： 1.50-4.99％，
Nb： 0.03-0.05％，
Mo： 0.15-0.25％，
Ti： 0.01-0.03％，
Si 0.15-0.25％，
Mn 0.40-0.50%, all the other are Fe and inevitable impurity, are all weight percentage above;
Wherein said steel alloy has bainite structure.
2. claim 1 containing Cr steel alloy, wherein,
The amount of C is 0.03-0.04%,
The amount 2.00-2.99% of Cr,
The amount of Nb is 0.03-0.05%,
The amount of Mo is 0.20-0.25%,
The amount of Ti is 0.02-0.03%, is all weight percentage above.
3. claim 1 containing Cr steel alloy, wherein,
The amount of C is 0.03-0.035%,
The amount of Cr is 3.01-4.99%,
The amount of Nb is 0.03-0.05%,
The amount of Mo is 0.20-0.25%,
The amount of Ti is 0.02-0.03%, is all weight percentage above.
4. any one of claim 1-3 containing Cr steel alloy, wherein, the amount of Si is 0.15-0.20wt%.
5. an oil gas pipeline, its making containing Cr steel alloy any one of claim 1-4.
6. manufacture the method containing Cr steel alloy, comprise the steps:
(1) provide the steel billet containing Cr steel alloy, described steel billet contains
C： 0.03-0.07％，
Cr： 1.50-4.99％，
Nb： 0.03-0.05％，
Mo： 0.15-0.25％，
Ti： 0.01-0.03％，
(2) forge described steel billet, wherein final forging temperature is not less than 1000 DEG C;
(3) steel billet through forging is made to carry out following two-phase control rolling,
A () first stage is rough rolling step, wherein the start rolling temperature of rough rolling step is 1100-1150 DEG C; The finishing temperature of rough rolling step is 980-1000 DEG C;
B () subordinate phase is the finish rolling stage, wherein the start rolling temperature in finish rolling stage is 900-950 DEG C; The finishing temperature in finish rolling stage is 850-900 DEG C;
The draft of wherein said rough rolling step is greater than 45%, and whole operation of rolling total reduction is not less than 65%;
(4) steel through rolling is cooled, obtain described steel alloy, wherein final cooling temperature is 500-600 DEG C, and speed of cooling is 10-35 DEG C/s.
7. the method for claim 6, when wherein forging described steel billet, first by after described heating steel billet to 1150-1200 DEG C also insulation, then carries out described forging.
8. the method for claim 6 or 7, wherein the draft of rough rolling step is greater than 50%.
9. the method any one of claim 6-7, wherein said steel billet contains
C：0.03-0.04％，
Cr：2.00-2.99％，
Nb：0.03-0.05％，
Mo：0.20-0.25％，
Ti:0.02-0.03%, is all weight percentage above.
10. the method any one of claim 6-7, wherein, described steel billet contains
C：0.03-0.035％，
Cr：3.01-4.99％，
Nb：0.03-0.05％，
Mo：0.20-0.25％，
Ti:0.02-0.03%, is all weight percentage above.
Method any one of 11. claim 6-7, wherein, the Si of described steel billet also containing 0.15-0.25wt%.
Method any one of 12. claim 6-7, wherein, the Si of described steel billet also containing 0.15-0.20wt%.
Method any one of 13. claim 6-7, wherein, the Mn of described steel billet also containing 0.40-0.60wt%.
Method any one of 14. claim 6-7, wherein, the Mn of described steel billet also containing 0.40-0.50wt%.
Method any one of 15. claim 6-7, wherein, described steel alloy has bainite structure.
The method of 16. claims 6, wherein, the start rolling temperature of rough rolling step is 1100-1130 DEG C.
The method of 17. claims 6, wherein, the finishing temperature of rough rolling step is 1000 DEG C.
The method of 18. claims 6, wherein, the start rolling temperature in finish rolling stage is 930-950 DEG C.
The method of 19. claims 6, wherein, the finishing temperature in finish rolling stage is 880-900 DEG C.
The method of 20. claims 6, wherein, final cooling temperature is 540-580 DEG C.
The method of 21. claims 6, when wherein forging described steel billet, first by after described heating steel billet to 1180-1200 DEG C also insulation, then carries out described forging.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110154407.6A CN102230133B (en) | 2011-06-09 | 2011-06-09 | Cr-containing Alloy steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110154407.6A CN102230133B (en) | 2011-06-09 | 2011-06-09 | Cr-containing Alloy steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102230133A CN102230133A (en) | 2011-11-02 |
| CN102230133B true CN102230133B (en) | 2015-05-13 |
Family
ID=44842736
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201110154407.6A Expired - Fee Related CN102230133B (en) | 2011-06-09 | 2011-06-09 | Cr-containing Alloy steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102230133B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104862607B (en) * | 2015-05-25 | 2017-01-18 | 北京科技大学 | Pipeline steel resistant to carbon dioxide corrosion and preparation method thereof |
| CN106011666A (en) * | 2016-06-03 | 2016-10-12 | 深圳市樊溪电子有限公司 | Low alloy steel, steel pipe and manufacturing method of steel pipe |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101353765A (en) * | 2007-07-23 | 2009-01-28 | 宝山钢铁股份有限公司 | Steel for CT80 grade coiled tubing, and manufacturing method and use thereof |
| CN101487101A (en) * | 2008-01-17 | 2009-07-22 | 宝山钢铁股份有限公司 | Steel for CT70 grade coiled tubing and method of manufacturing the same |
| CN102071361A (en) * | 2009-11-20 | 2011-05-25 | 宝山钢铁股份有限公司 | Steel for high temperature resistant oil well tube and manufacturing method thereof |
-
2011
- 2011-06-09 CN CN201110154407.6A patent/CN102230133B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101353765A (en) * | 2007-07-23 | 2009-01-28 | 宝山钢铁股份有限公司 | Steel for CT80 grade coiled tubing, and manufacturing method and use thereof |
| CN101487101A (en) * | 2008-01-17 | 2009-07-22 | 宝山钢铁股份有限公司 | Steel for CT70 grade coiled tubing and method of manufacturing the same |
| CN102071361A (en) * | 2009-11-20 | 2011-05-25 | 宝山钢铁股份有限公司 | Steel for high temperature resistant oil well tube and manufacturing method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 胡丽华 等.Cr含量对低合金耐蚀管线钢焊接接头组织和性能的影响.《材料热处理学报》.2010,第31卷(第3期), * |
| 胡丽华 等.含铬管线钢的显微组织和力学性能.《机械工程材料》.2010,第34卷(第12期),第51-58页. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102230133A (en) | 2011-11-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5574059B2 (en) | High-strength H-section steel with excellent low-temperature toughness and method for producing the same | |
| CN109957712B (en) | Low-hardness X70M pipeline steel hot-rolled plate coil and manufacturing method thereof | |
| CN101864536B (en) | Q 390E class super-thick steel plate with thickness of 100mm and manufacturing method thereof | |
| CN102373387B (en) | Steel plate for large-strain cold-bent tube and manufacturing method thereof | |
| CN112813353B (en) | Steel for ultra-high temperature SPWHT high-toughness normalizing container and manufacturing method thereof | |
| CN101619416A (en) | High-strength X100 pipeline steel hot-rolled flat plate and production method thereof | |
| WO2011132765A1 (en) | Cr-CONTAINING STEEL PIPE FOR LINE PIPE AND HAVING EXCELLENT INTERGRANULAR STRESS CORROSION CRACKING RESISTANCE AT WELDING-HEAT-AFFECTED PORTION | |
| CN101906575A (en) | High-strength economical X70 pipeline steel hot-rolled flat plate and production method thereof | |
| CN101514435B (en) | Pipeline steel with good and stable low-temperature flexibility and method for rolling hot rolled coils thereof | |
| CN104937125B (en) | The effective hot rolled steel plate of high-strength line-pipe steel | |
| CN110129658A (en) | A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and preparation method | |
| CN102260834A (en) | H2S corrosion resistant hot rolled steel plate for oil well pipe and preparation method thereof | |
| CN1318631C (en) | Method for producing high strength high toughness X80 pipeline steel and its hot-rolled plate | |
| AU2022208884A1 (en) | High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor | |
| CN101413090B (en) | High-strength high-toughness X80 hot rolling coiled sheet for spiral buried arc welding and production method thereof | |
| CN103993245A (en) | Low-carbon equivalent high-strength hot-rolled seamless pipeline tube and manufacturing method thereof | |
| CN103469097B (en) | The corrosion-resistant tubing and casing of high strength martensitic ferrite diphasic stainless steel and manufacture method thereof | |
| CN109536838B (en) | Needle-shaped ferrite type low-temperature-resistant N80-grade petroleum casing steel and preparation method thereof | |
| CN103602903A (en) | High-strength carbon dioxide corrosion-resisting oil well pipe and manufacturing method thereof | |
| CN106929774A (en) | A kind of normalizing state X52 sulfur resistive seamless line pipes and preparation method thereof | |
| CN105695882B (en) | J55-grade low-yield-ratio electric resistance welding sleeve steel and manufacturing method thereof | |
| CN102230133B (en) | Cr-containing Alloy steel and manufacturing method thereof | |
| CN101705438A (en) | X70 hot-rolled steel coil for pipeline steel and manufacturing method thereof | |
| JP4022991B2 (en) | Ferritic-martensitic duplex stainless steel pipe | |
| CN115369323B (en) | 800 MPa-level hydrogen-induced crack resistant container steel plate and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20150513 Termination date: 20200609 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |