CN104862591A - Steel for high-strength high-pressure oil pipe, high-pressure oil pipe and manufacturing method of high-pressure oil pipe - Google Patents
Steel for high-strength high-pressure oil pipe, high-pressure oil pipe and manufacturing method of high-pressure oil pipe Download PDFInfo
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Abstract
The invention discloses steel for a high-strength high-pressure oil pipe, which comprises the following chemical elements by mass percent: 0.11-0.17% of C, 0.1-0.5% of Si, 1.2-1.7% of Mn, 0.01-0.05% of Al, 0.01-0.06% of Nb, 0.02-0.09% of V, 0.001-0.03% of Ti, 0.001-0.01% of Ca and the balance of Fe and other inevitable impurities. Correspondingly, the invention further discloses the high-pressure oil pipe manufactured by the steel for the high-strength high-pressure oil pipe. In addition, the invention further discloses a manufacturing method of the oil pipe. The steel for the high-strength high-pressure oil pipe and the high-pressure oil pipe have high strength and good low-temperature toughness.
Description
Technical field
The present invention relates to a kind of steel grade and manufacture method thereof, particularly relate to a kind of oily tube steel and manufacture method thereof.
Background technology
Along with increasing the weight of of world energy sources crisis and environmental pollution, in order to save energy, reduce discharge, new work engine must use high pressure co-rail system.In common rail fuel combustion system, by injection pump, high pressure fuel is transported to common feeder line, by realizing the oil pressure in common feeder line accurately controlling, the rotating speed of high pressure pipe pressure size and engine is had nothing to do, significantly can reduce the change of Fuel Injection Mechanism of Diesel Engine pressure with motor speed, make engine can obtain very high fuel pressure in all speed range, the pressure ratio conventional diesel engine of this injection system to exceed 3 times, most high energy reaches 200MPa (and conventional diesel engine injection oil pressure is at 60-70MPa).
In whole hydraulic efficiency system, the spraying pressure improved constantly is had higher requirement to high-pressure line bearing capacity in use.High-pressure line is responsible for conveying high-pressure diesel oil, while bearing high operating pressure, also by the alternative cycle stress of hydraulic efficiency oil repeated stock, very easily produces fatigue failure; Simultaneously high-pressure line belongs to the tubing typically bearing inner high voltage, and the stress that endoporus oil pressure is formed on fuelpipe cross section is uneven along thickness of pipe distribution, and circumference (tangentially) stress on inner surface of tube wall, radial stress are all in peak level.Therefore, the longitudinal cracking originating from fuelpipe bore surface is the possible main failure forms of high-pressure line.For this reason, the material developing more high strength grade is the effective way promoting high-pressure line bearing capacity.
At present, the high-pressure line material of 3 strength grades is defined in ISO8535-1 " the effective steel pipe first part of diesel motor-high pressure fuel injection: the seamless cold single wall steel pipe requires " standard that European Countries is generally quoted, the trade mark 16Mn, 16MnV etc. in corresponding country, its high-pressure line made is applicable to the operating pressure of below 160MPa.
In addition, publication number is CN104141097A, publication date is on November 12nd, 2014, the Chinese patent literature of title " a kind of high-pressure line hot rolled circular steel and manufacture method thereof " discloses a kind of high-pressure line, its chemical composition mass percent (wt%) is: C:0.10-0.17%, Si:0.25-0.45%, Mn:1.30-1.60%, P≤0.020%, S≤0.010%, Cr:0.20-0.40%, V:0.05-0.10%, Al:0.025-0.050%, Cu :≤0.20%, Ni≤0.20%, all the other are iron and remaining trace impurity.Disclosed in this sharp document, the intensity of oily tube steel is lower than the technical program.
Summary of the invention
The object of the present invention is to provide a kind of high-strength high-voltage oil tube steel, it also has excellent low-temperature flexibility while meeting more than yield strength 600MPa.
To achieve these goals, the present invention proposes a kind of high-strength high-voltage oil tube steel, its chemical element mass percentage content is:
C：0.11-0.17％；
Si：0.1-0.5％；
Mn：1.2-1.7％；
Al：0.01-0.05％；
Nb：0.01-0.06％；
V：0.02-0.09％；
Ti：0.001-0.03％；
Ca：0.001-0.01％；
Surplus is Fe and other inevitable impurity.
The principle of design of each chemical element in high-strength high-voltage oil tube steel of the present invention is:
C is the one of the chief elements of the intensity improving steel, and its formation by carbide can improve the intensity of steel effectively, and it is low to add cost.In the technical program, when C content is lower than 0.11wt.%, weldless steel tube can not reach the intensity of more than 600MPa, but when C content higher than 0.17% time, the low temperature impact properties of weldless steel tube can be affected.Therefore, need the content of C element to control to be 0.11 ~ 0.17% in the present invention.
Si is as reductive agent and reductor in steelmaking process, and it does not form carbide in steel, and its solid solubility in steel is comparatively large, can strengthen ferrite in steel to improve the intensity of steel.But in the technical program, once silicone content is more than 0.5%, greatly can reduce the toughness of steel pipe, especially the low-temperature impact toughness of steel pipe.Therefore, need Si content to control to be 0.10 ~ 0.5%.
Mn improves the intensity of steel mainly through solution strengthening.Increasing Mn content can make the transformation temperature of steel reduce, and reduces phase transformation critical cooling velocity, when Mn content reaches more than 1.2%, can enlarge markedly the hardening capacity of steel; But, if when Mn content is more than 1.7%, the impelling strength of steel declines comparatively remarkable thereupon.So need Mn content to be set as 1.2 ~ 1.7% in the technical program.
Al has desoxydatoin in steel and it contributes to improving toughness and the processibility of steel.In the technical program, when Al content reaches more than 0.01%, its effect improving the toughness of steel and processibility is comparatively remarkable, but when Al content is more than 0.05%, difficulty of making steel significantly increases.The present invention is based on this and Al content is controlled between 0.01 ~ 0.05%.
Nb is strong carbonitride-forming elements, and can postpone austenite recrystallization during hot rolling and reach the effect of crystal grain thinning, reheating in process, it can hinder Austenite Grain Growth.In the technical program, when Nb content >=0.01%, above-mentioned useful additive effect is obvious, and when not excessive Nb content is more than 0.06%, the toughness of steel can decrease on the contrary.Therefore, Nb content should be set as 0.01 ~ 0.06% by the present invention.
V is the forming element of strong carbide, and the binding ability of itself and carbon is very strong, and the VC particle of its small and dispersed formed can play the effect of dispersion-strengthened, and the intensity of steel is obviously increased.If the content of V is less than 0.02%, its dispersion-strengthened action is also not obvious, but if the content of V is greater than 0.09%, then the toughness of steel can be caused to decline.For this reason, the content of the V in the technical program control steel is 0.02 ~ 0.09%.
Ti is also strong carbonitride-forming elements, and its TiN, TiC formed is in soaking and reheat all can fining austenite grains in process.But, if Ti content is too high, then easily form thick TiN.Therefore Ti content controls as 0.001-0.03% by the present invention.
Ca can cleaning molten steel, makes inclusion modification to control the distributional pattern of sulfide, thus reaches the object obtaining tiny spherical, sulfide that disperse is uniform.In order to realize this object, the present invention's control Ca content is 0.001 ~ 0.01%.
Inevitable impurity mainly S, P, O, N element in the technical program.These impurity elements easily form inclusion, the inclusion of formation on the one hand to the intensity of material and toughness unfavorable, easily cause on the other hand producing defect so that fracture during cold working, therefore must strict restriction.
Therefore, preferably, control P≤0.015% as far as possible, O≤0.003%, S≤0.005%, N≤0.004%.
High-strength high-voltage oil tube steel of the present invention is not containing the Addition ofelements that the cost such as Mo, Ni or rare earth metal is higher, it is by the optimization design to chemical composition, in conjunction with follow-up rational manufacturing process, make the intensity high and low temperature good toughness of high-pressure line of the present invention, and with low cost.
Further, the microtexture of high-strength high-voltage oil tube steel of the present invention is the ferrite+tempered sorbite containing dislocation born of the same parents.
Dislocation born of the same parents are born of the same parents' shape substructure that dislocation is formed, and above-mentioned microtexture makes steel of the present invention also have high strength and good low-temperature toughness while reaching dislocations strengthening effect.Dislocation is the dislocation of crystal lattices arrangement.Cold deformation can make the dislocation fast breeding in Metallic Solids, and when dislocation desity is very high, dislocation tangling and form similar cellulated subgrain structure, i.e. dislocation born of the same parents, this technical term is that those skilled in that art know, therefore is not described in detail at this.
Further, the microtexture of high-strength high-voltage of the present invention oil tube steel also have the precipitate of the Nb of Dispersed precipitate, the precipitate of V, the precipitate of Ti at least one of them.
Further, the precipitate of described Ti comprises Ti (C, N) (i.e. the carbonitride of titanium).
Further, the precipitate of described V comprises VC.
Further, the precipitate of described Nb comprises Nb (C, N) (i.e. the carbonitride of niobium).
Yield strength >=the 600MPa of high-strength high-voltage oil tube steel of the present invention ,-20 DEG C of low-temperature impact work >=34J, unit elongation > 16%.
Another object of the present invention is to provide a kind of high-strength high-voltage oil pipe, it is weldless steel tube, and it adopts high-strength high-voltage oil pipe steel as herein described to obtain.
Further, the external diameter of high-strength high-voltage oil pipe of the present invention is 8-10mm, and its caliber than existing high-pressure line is little.
Further, the wall thickness of high-strength high-voltage oil pipe of the present invention is 1.5-3mm.
Another object of the present invention is the manufacture method providing a kind of above-mentioned high-strength high-voltage oil pipe, and it comprises step:
(1) pipe is manufactured;
(2) by soaking after heating of pipe blank;
(3) hot piercing and tension reducing, then naturally cooling;
(4) pickling, phosphatization and saponification;
(5) cold-drawn or cold rolling mode is adopted to carry out cold working;
(6) stress relief annealing.
Further, in described step (1), by heating of pipe blank to 1200 DEG C-1260 DEG C, soaking 30-90min.
Further, in described step (5), the cold working of several passages is carried out; Wherein the cold working coefficient of extension of last passage is 1.6-2.1, to ensure that steel pipe obtains enough drawing hardening effect before final stress relief annealing step, the cold worked coefficient of extension of other passages is in addition greater than 0 and is less than or equal to 1.5, thus while guarantee steel pipe's production efficiency, avoid the steel pipe after cold working to produce the defects such as cracking; And carry out softening thermal treatment between two adjacent passages, wherein the softening thermal treatment temp of last passage is 740-800 DEG C, the type of cooling is water smoke cooling, and speed of cooling is 5-30 DEG C/s; The softening thermal treatment temp of other passages is in addition 760-800 DEG C, and the type of cooling is air cooling; Thus make the intermediate structure of acquisition ferrite+bainite after step (5) completes.
Further, in described step (6), stress relief annealing temperature 500-600 DEG C, soaking time is 30-90min.
The Heating temperature of above-mentioned stress relief annealing is too high, or the long dislocation born of the same parents that steel pipe all can be caused to produce in cold working process of soaking time disappear, and the intensity of steel pipe is significantly declined.But the too low unrelieved stress that cold working process can not be made again to produce of the temperature of stress relief annealing is eliminated, and can not reach service requirements by causing the low-temperature flexibility of material.At this, the stress relief annealing temperature in the manufacture method of high-pressure line of the present invention is set as 500-600 DEG C, and to control soaking time be 30-90min.
Alternatively, in the manufacture method of high-strength high-voltage oil pipe of the present invention, between described step (4) and step (5), also there is intermediate heat treatment step, thus ensure the cold-forming property of steel pipe further.
High-pressure oil tube steel of the present invention is owing to have employed technique scheme, make it while possessing high strength, also have good low-temperature flexibility, its yield strength >=600MPa ,-20 DEG C of low-temperature impacts absorb merit >=34J, unit elongation > 16%.
High-strength high-voltage oil pipe of the present invention has above-mentioned beneficial effect equally.In addition, the caliber of high-strength high-voltage oil pipe of the present invention is little, and cost performance is high.
Accompanying drawing explanation
The intermediate structure that the steel pipe that Fig. 1 shows embodiment of the present invention A3 obtains after the softening thermal treatment having carried out last passage.
Fig. 2 shows the microtexture of the fished pipe of embodiment of the present invention A3.
Fig. 3 amplification shows the dislocation cell structure with born of the same parents' shape substructure in the ferrite in Fig. 2.
Embodiment
Illustrate below in conjunction with accompanying drawing and with specific embodiment, high-strength high-voltage of the present invention oil tube steel, high-strength high-voltage oil pipe and manufacture method thereof to be made further explanation, but this explanation and explanation do not form improper restriction to technical scheme of the present invention.
Embodiment A 1-A7 and comparative example B1-B4.
Manufacture the oil pipe of high-strength high-voltage oil pipe in embodiments of the invention A1-A7 and comparative example B1-B4 according to the following step, concrete steps comprise:
(1) smelt and make pipe, the chemical element percent mass proportioning controlled in steel is as shown in table 1;
(2) adopt rotary heating furnace by heating of pipe blank to 1200 DEG C-1260 DEG C, soaking 30-90min;
(3) adopt vertical conical hot punching machine to carry out hot piercing, by three-roller tension reducing mill, tube reducing is carried out to pipe and subtract naturally cooling after wall thickness;
(4) phosphatization saponification again after pickling is carried out to steel pipe;
(5) cold-drawn or cold rolling mode is adopted to carry out the cold working of N number of passage, wherein, first to every time cold worked coefficient of extension≤1.5 (nonzero value) of N-1 passage, last passage cold working coefficient of extension is within the scope of 1.6-2.1, steel pipe final dimension after cold working is wall thickness 1.5-3mm, external diameter 8-10mm, in addition, also need to carry out softening thermal treatment (namely to the heat treatment step that distortion ferrite softens) between two adjacent passages, namely the cold working of corresponding N number of passage needs the softening thermal treatment carrying out N-1 passage, softening thermal treatment (the i.e. softening thermal treatment of N-1 passage wherein before last passage cold working, also the softening thermal treatment of i.e. last passage) temperature be 740-800 DEG C, then water smoke accelerating cooling is carried out to steel pipe, cooling rate 5-30 DEG C/s, to obtain ferrite+bainite structure, the temperature of the softening thermal treatment of other N-2 passage (namely first passage is to the softening thermal treatment of N-2 passage) is 760-800 DEG C, then air cooling,
(6) stress relief annealing: stress relief annealing temperature 500-600 DEG C, soaking time is air cooling after 30-90min, and the microtexture of acquisition fished pipe is the ferrite+tempered sorbite containing dislocation born of the same parents.
It should be noted that, suitable intermediate heat treatment technique can also be adopted to ensure the cold-forming property of steel pipe further before above-mentioned steps (5).
Fig. 1 shows the intermediate structure of the steel pipe obtained after last passage thermal treatment in embodiment A 3, and as can be seen from the figure now the microtexture of steel pipe is ferrite+bainite.
Fig. 2 shows the microtexture of the fished pipe in embodiment A 3, and as can be seen from the figure, the microtexture of this steel pipe finished product is the ferrite+tempered sorbite containing dislocation born of the same parents.
Fig. 3 amplifies the dislocation cell structure with born of the same parents' shape substructure shown in the ferrite shown in Fig. 2 further.
Table 1 lists the chemical element percent mass proportioning of the steel pipe in this case embodiment A 1-A7 and comparative example B1-B4.
Table 1. (wt.%, surplus is Fe and other the inevitable impurity except S, O, P, N)
| Sequence number | C | Si | Mn | Al | Nb | V | Ti | Ca | P | S | O | N |
| A1 | 0.11 | 0.1 | 1.5 | 0.01 | 0.01 | 0.09 | 0.001 | 0.001 | 0.009 | 0.003 | 0.0016 | 0.002 |
| A2 | 0.15 | 0.5 | 1.7 | 0.03 | 0.03 | 0.02 | 0.03 | 0.002 | 0.012 | 0.004 | 0.0022 | 0.001 |
| A3 | 0.14 | 0.45 | 1.5 | 0.05 | 0.04 | 0.06 | 0.005 | 0.003 | 0.008 | 0.001 | 0.0017 | 0.003 |
| A4 | 0.16 | 0.15 | 1.3 | 0.03 | 0.06 | 0.03 | 0.01 | 0.009 | 0.014 | 0.002 | 0.0018 | 0.004 |
| A5 | 0.17 | 0.2 | 1.2 | 0.02 | 0.05 | 0.04 | 0.02 | 0.01 | 0.007 | 0.005 | 0.0024 | 0.003 |
| A6 | 0.13 | 0.37 | 1.4 | 0.02 | 0.02 | 0.08 | 0.002 | 0.005 | 0.006 | 0.004 | 0.002 | 0.002 |
| A7 | 0.12 | 0.5 | 1.6 | 0.02 | 0.03 | 0.04 | 0.02 | 0.004 | 0.01 | 0.005 | 0.0022 | 0.004 |
| B1 | 0.16 | 0.35 | 1.4 | 0 | 0 | 0 | 0 | 0 | 0.02 | 0.01 | 0.006 | 0.008 |
| B2 | 0.16 | 0.35 | 1.4 | 0 | 0 | 0.11 | 0 | 0 | 0.02 | 0.01 | 0.005 | 0.007 |
| B3 | 0.09 | 0.5 | 1.6 | 0.02 | 0.03 | 0.04 | 0.02 | 0.004 | 0.01 | 0.005 | 0.0022 | 0.004 |
| B4 | 0.16 | 0.35 | 1.4 | 0.04 | 0 | 0.08 | 0 | 0 | 0.008 | 0.004 | 0.005 | 0.006 |
Note: the Cr element also containing 0.3% in B4.
Table 2 shows the concrete technology parameter of each step in this case embodiment A 1 ~ A7 and comparative example B1 ~ B4.
Table 2.
Steel pipe in above-described embodiment and comparative example is produced the impact specimen being of a size of 2mm*10mm*55mm along rolling direction, and be that after the standard v-notch of 2mm, each impact toughness value obtained after testing at-20 DEG C is listed in table 3 in the side opening degree of depth.In addition, table 3 also list intensity and the unit elongation of each steel pipe in embodiment and comparative example.
Table 3.
Associative list 1, table 2 and table 3 can be found out, because each weldless steel tube in this case embodiment A 1-A7 has the chemical element percent mass proportioning of technical scheme defined of the present invention, and it all carries out processing according to manufacture method provided by the present invention, the yield strength of the high-pressure line therefore in embodiment A 1-A7 is all greater than 600MPa, the equal > 16% of unit elongation.In addition, this high-pressure line is minimum at the impact absorbing energy of-20 DEG C is 34J.But, because some the chemical element percent mass proportioning in each weldless steel tube in comparative example B1-B4 has exceeded technical scheme limited range of the present invention, therefore, at least one item in the comprehensive mechanical property of these weldless steel tubes can not reach the implementation result of this case.
From the content shown in above table, technical scheme of the present invention, by the heat treatment mode of reasonable component design+reasonably cold machining process+optimization, obtains the weldless steel tube of intensity high and low temperature impact property and good percentage elongation.This type of weldless steel tube is particularly useful for manufacturing high-pressure line.
It should be noted that above enumerate be only specific embodiments of the invention, obviously the invention is not restricted to above embodiment, have many similar changes thereupon.If all distortion that those skilled in the art directly derives from content disclosed by the invention or associates, protection scope of the present invention all should be belonged to.
Claims (16)
1. a high-strength high-voltage oil tube steel, it is characterized in that, its chemical element mass percentage content is:
C：0.11-0.17％；
Si：0.1-0.5％；
Mn：1.2-1.7％；
Al：0.01-0.05％；
Nb：0.01-0.06％；
V：0.02-0.09％；
Ti：0.001-0.03％；
Ca：0.001-0.01％；
Surplus is Fe and other inevitable impurity.
2. high-strength high-voltage oil tube steel as claimed in claim 1, it is characterized in that, its microtexture is the ferrite+tempered sorbite containing dislocation born of the same parents.
3. high-strength high-voltage oil tube steel as claimed in claim 2, is characterized in that, its microtexture also have the precipitate of the Nb of Dispersed precipitate, the precipitate of V, the precipitate of Ti at least one of them.
4. high-strength high-voltage oil tube steel as claimed in claim 3, it is characterized in that, the precipitate of described Ti comprises Ti (C, N).
5. intensity high-pressure oil tube steel as claimed in claim 3, it is characterized in that, the precipitate of described V comprises VC.
6. intensity high-pressure oil tube steel as claimed in claim 3, it is characterized in that, the precipitate of described Nb comprises Nb (C, N).
7. high-strength high-voltage oil tube steel as claimed in claim 1, is characterized in that, P≤0.015% in described inevitable impurity, O≤0.003%, S≤0.005%, N≤0.004%.
8. high-strength high-voltage oil tube steel as claimed in claim 1, is characterized in that, its yield strength >=600MPa ,-20 DEG C of low-temperature impact work >=34J, unit elongation > 16%.
9. a high-strength high-voltage oil pipe, it is weldless steel tube, it is characterized in that, it adopts as the high-strength high-voltage oil pipe steel in claim 1-8 as described in any one obtains.
10. high-strength high-voltage oil pipe as claimed in claim 9, it is characterized in that, its external diameter is 8-10mm.
11. high-strength high-voltage oil pipes as claimed in claim 10, it is characterized in that, its wall thickness is 1.5-3mm.
The manufacture method of 12. high-strength high-voltage oil pipes as claimed in claim 9, it comprises step:
(1) pipe is manufactured;
(2) by soaking after heating of pipe blank;
(3) hot piercing and tension reducing, then naturally cooling;
(4) pickling, phosphatization and saponification;
(5) cold-drawn or cold rolling mode is adopted to carry out cold working;
(6) stress relief annealing.
The manufacture method of 13. high-strength high-voltage oil pipes as claimed in claim 12, is characterized in that, in described step (1), by heating of pipe blank to 1200 DEG C-1260 DEG C, and soaking 30-90min.
The manufacture method of 14. high-strength high-voltage oil pipes as claimed in claim 12, is characterized in that, in described step (5), carry out the cold working of several passages; Wherein the cold working coefficient of extension of last passage is 1.6-2.1, and the cold worked coefficient of extension of other passages is in addition greater than 0 and is less than or equal to 1.5; And carry out softening thermal treatment between two adjacent passages, wherein the softening thermal treatment temp of last passage is 740-800 DEG C, the type of cooling is water smoke cooling, and speed of cooling is 5-30 DEG C/s; The softening thermal treatment temp of other passages is in addition 760-800 DEG C, and the type of cooling is air cooling; Thus make the intermediate structure of acquisition ferrite+bainite after step (5) completes.
The manufacture method of 15. high-strength high-voltage oil pipes as claimed in claim 12, is characterized in that, in described step (6), stress relief annealing temperature 500-600 DEG C, soaking time is 30-90min.
The manufacture method of 16. high-strength high-voltage oil pipes as claimed in claim 12, is characterized in that also having intermediate heat treatment step between described step (4) and step (5).
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