CN107964637A - A kind of CT100 grades of connecting pipes hot rolled strip and production method - Google Patents
A kind of CT100 grades of connecting pipes hot rolled strip and production method Download PDFInfo
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- CN107964637A CN107964637A CN201711325095.4A CN201711325095A CN107964637A CN 107964637 A CN107964637 A CN 107964637A CN 201711325095 A CN201711325095 A CN 201711325095A CN 107964637 A CN107964637 A CN 107964637A
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
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- 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
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- 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
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- C21D2211/002—Bainite
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- Mechanical Engineering (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A kind of CT100 grades of connecting pipes hot rolled strip, its component and wt%：C：0.10~0.14%, Si：0.10~0.30%, Mn：1.10~1.50%, P：≤ 0.015%, S：≤ 0.0020%, Cu：0.25~0.40%, Ni：0.15~0.35%, Cr：0.60~1.00%, Nb：0.020~0.050%, V：≤ 0.010%, Ti：0.010~0.030%, N：≤ 0.0050%, Al：0.015~0.060%, Ca：0.0008~0.0025%.Production stage：Base is casting continuously to form after the processes such as converter smelting；To heating strand；Roughing；Finish rolling；Cool down and batch.The theoretical depth of implements of the present invention is up to 7000m, actual job depth at least increases by 450 meters, working pressure in well is up to 90 MPa, its yield strength >=640MPa, tensile strength >=740MPa, full thickness of slab hardness fluctuations≤23HV1.0, yield tensile ratio≤0.88, elongation percentage >=18%, section vickers hardness hv 1.0≤270,20 DEG C of low-temperature flexibilities are higher than 100J, and are inclined to without surface copper brittleness.
Description
Technical field
The present invention relates to a kind of pipe line steel and production method, belongs to a kind of theoretical depth of implements and reaches 7000m, underground work pressure
Power reaches the CT100 level connecting pipes hot rolled strips and production method of 90MPa.
Background technology
Continuous pipe is the novel tube for petroleum drilling and mining industry, and pipe is coiled in up to the flexible steel pipe of the supreme myriametre of thousands of rice
On disk, when operation, opens from pipe dish, is coiled in again in pipe dish after operation, can Reusability.Compared to conventional oil well
Pipe, continuous oil pipe operation is more flexible, have Operating Pressure, continuously remove, equipment volume is small, duty cycle is fast, cost is low
Advantage.
Before making the present invention, have：
Chinese Patent Application No. be 201611162208.9 document, disclose " a kind of CT90 grades of connecting pipes hot rolled strip and
Its production method ", the product strength level is relatively low, and in ultradeep well operation process, it is difficult to bear big dead weight, and
The high pressure of steel duct in operation process, with the continuous pipe of the production, its theoretical depth of implements is only capable of reaching 6000m, real
Border depth of implements is at 3500 meters, and the continuous pipe of this patent production requires theoretical depth of implements to reach 7000m, underground work pressure
Power reaches 90MPa.
Chinese Patent Application No. be 200710168545.3 document, disclose " a kind of steel for high-plasticity continuous oil pipe and
Its manufacture method ", it contains part ferrite and pearlite in organizing, this significantly reduces its steel band intensity, according to its whole
Embodiment, yield strength≤590MPa, tensile strength≤700MPa, too low intensity determine that it can not be suitable for ultradeep well and make
Industry；In addition, its alloy and design are so that its steel strip surface easily induces fatigue crack, this can significantly in the presence of the possibility that copper brittleness occurs
The fatigue life of steel pipe is reduced, is also unfavorable safely to underground work.
Chinese Patent Application No. be 200810040895.6 document, disclose " a kind of CT90 cascades steel for continuous oil pipe and
Its manufacture method ", its intensity are equally insufficient for the needs of ultra-deep well operations；At the same time containing higher in its its composition design
V, this toughness and welding performance to product is unfavorable；For its steel plate yield tensile ratio more than 0.90, deformability is poor, can not
Meet to need the requirement being plastically deformed repeatedly in such product operation process.
The content of the invention
It is insufficient present in above-mentioned document it is an object of the invention to overcome, there is provided a kind of depth of implements increases than the prior art
Add and do not surpass up to 90MPa, yield strength >=640MPa, tensile strength >=740MPa, yield tensile ratio no less than 450m, working pressure in well
0.88 is crossed, elongation percentage A50mm（Tensile sample parallel portion width b=12.5mm）>=18%, section vickers hardness hv 1.0≤270, and
Full thickness of slab hardness fluctuations are less than 23HV1.0, CT100 level connecting pipes hot rolled strip of -20 DEG C of low-temperature flexibilities higher than 100J and life
Production method.
Realize the measure of above-mentioned purpose：
A kind of CT100 grades of connecting pipes hot rolled strip, its component and weight percent content are：C：0.10~0.14%, Si：
0.10~0.30%, Mn：1.10~1.50%, P：≤ 0.015%, S：≤ 0.0020%, Cu：0.25~0.40%, Ni：0.15~
0.35%, Cr：0.60~1.00%, Nb：0.020~0.050%, V：≤ 0.010%, Ti：0.010~0.030%, N：≤
0.0050%, Al：0.015~0.060%, Ca：0.0008~0.0025%, surplus is Fe and is inevitably mingled with.
Preferably：The Cu weight percent contents are 0.28~0.36%.
Preferably：The Ni weight percent contents are 0.18~0.32%.
Preferably：The Cr weight percent contents are 0.65~0.93%.
Preferably：The Ca weight percent contents are 0.00092~0.002%.
Produce a kind of method of CT100 grades of connecting pipes hot rolled strip, its step：
1）Base is casting continuously to form after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to no more than 450
℃；
2）To heating strand, heating and temperature control keeps the temperature 60~90min at this temperature at 1260~1320 DEG C；
3）Roughing is carried out, rolling pass is 6 passages, and controls its end temp at 1050~1120 DEG C；
4）Finish rolling is carried out, and controls finishing temperature at 850~920 DEG C, finish rolling total reduction is not less than 85%；
5）Cooled down：Cooling velocity be 70~120 DEG C/s under be cooled to 550~650 DEG C, after be air-cooled to 500~600 DEG C again
Batched.
The effect of each element and mechanism in the present invention
Carbon（C）：Most economical intensified element, the intensity of steel is lifted by gap solution strengthening.Increase carbon content, can be substantially improved
The quenching degree of steel, reduces the addition of other precious alloys, reduces production cost, while the yield tensile ratio to reducing steel is beneficial, because
This C content is unsuitable too low.But carbon content is higher, more it is unfavorable for the low-temperature flexibility of steel, while is easily formed in steel grade more serious
Hard phase segregation band, aggravates the structural heterogenity of steel, is unfavorable for the fatigue behaviour of product, therefore carbon content also can not be excessive.Compared with
The additive amount of suitable carbon is 0.10~0.14%.
Silicon（Si）：Solution strengthening effect is mainly played, is beneficial to aid in desulfurization in smelting process, is also advantageous for the tired of lifting steel
Labor performance.But during too high levels, it is unfavorable for surface quality, easily leads to the iron scale in the operation of rolling and be difficult to remove.Conveniently
Silicon additive amount be 0.10~0.30%.
Manganese（Mn）：Relatively inexpensive alloy element, can be obviously improved surrender and the tensile strength of steel.But manganese content is higher
When, such as inappropriate technology, is also easy to produce more serious microstructure segregation, causes component, the tissue odds of steel.The additive amount of convenient manganese
For 1.10~1.50%.
Phosphorus, sulphur, nitrogen（P、S、N）：Phosphorus easily leads to the cold short of steel, and sulphur easily causes hot-short, and nitrogen easily causes the quenching of steel to be failed
Fail with deformation, cause the performance of steel unstable, therefore should the try one's best phosphorus reduced in steel, sulphur, the content of nitrogen.
Copper, nickel（Cu、Ni）：The intensity of steel can be lifted by solution strengthening, mainly being risen in this copper improves the anti-corrosion weather-proof of steel
The effect of performance, general addition are more than 0.25%；Nickel can improve the red brittleness because adding copper, and general addition is copper content
More than 2/3.Preferably：Cu weight percent contents are that 0.28~0.36%, Ni weight percent contents are 0.18~0.32%.
Chromium（Cr）：The effectively quenching degree of lifting steel, and there is certain solution strengthening effect.Chromium can be in corrosive environment
The surface of steel forms comparatively dense protective layer, plays the role of protecting matrix, effectively improves steel corrosion resistance.But chromium in steel
During too high levels, it is unfavorable for high-frequency resistance welding (HFRW) weldquality, easily forms flat spot, it is necessary to using welding protection, adds weldering
Connect difficulty and cost.The additive amount of convenient easy welding connecting pipes steel chromium is 0.60~1.00%.Preferably Cr weight percents
It is 0.65~0.93% than content.
Niobium, titanium（Nb、Ti）：Micro alloying element, significantly crystal grain thinning and can play the role of precipitation strength, be remarkably improved
The austenite recrystallization temperature of steel, expands Unhydrated cement scope, is easy to implement high temperature controlled rolling, reduces mill load.It is but limited
Designed in carbon content, when niobium, Ti content are excessive, be not only difficult to play one's part to the full, while precipitation particle may be caused thick not
Beneficial to the toughness of steel.Convenient niobium, the additive amount of titanium are respectively 0.020~0.050%, 0.010~0.030%.
Aluminium（Al）：Aluminium is deoxidant element main in steel, can significantly reduce the oxygen content in steel, while the knot of aluminium and nitrogen
Conjunction forms AlN, being capable of effectively crystal grain thinning.But when aluminium content is more than 0.06% in steel, easily lead to aluminium oxide be mingled with it is bright
Aobvious increase, reduces the cleanliness factor of steel, unfavorable to the low-temperature flexibility of steel.The additive amount of convenient aluminium is respectively 0.015~
0.060%。
Calcium（Ca）：Calcium treatment is carried out to steel during double refining, the inclusion morphology in steel can be improved, improves steel
Impact flexibility, but excessive, the easy cleanliness factor for reducing steel is added, it is unfavorable to the low-temperature flexibility of steel.Therefore control additive amount is 0.0008
~0.0025%.Preferably Ca weight percent contents are 0.00092~0.002%.
In the present invention, why heating-up temperature is located at 1260~1320 DEG C of scopes to carry out, and kept the temperature at this temperature
60~90min, is the homogenization for realizing the easily segregation-alloy element such as Mn, Cr, improves the micro components segregation of steel billet, finally change
The uniformity of the final microstructure of kind steel band.But when heating-up temperature is less than 1260 DEG C, element microsegregation improvement is not shown
Write, or need long soaking time to realize the diffusion-homogenization of alloying element, so as to cause production efficiency to be greatly reduced；
And as heating-up temperature increases, austenite grain is gradually roughened, when heating-up temperature is higher than 1320 DEG C（Or heating-up temperature is higher than
1300 DEG C, but during heating and thermal insulation overlong time）, austenite grain is excessively roughened, and causes final products coarse grains and surrender
Intensity deficiency.Therefore, convenient heating-up temperature is at 1260~1320 DEG C, preferred heating-up temperature at 1260~1300 DEG C,
Soaking time is in 60~90min.
Why total reduction >=85% of finish rolling is set in the present invention, the fine that is to realize steel band tissue and uniformly
Change.Limited by existing general producing line capacity of equipment, the open rolling in finish rolling stage of the present invention and finishing temperature setting are of a relatively high, to subtract
Few rolling load, and then guarantee smoothly to produce.But when final rolling temperature is higher, steel band finishing stands can be caused to include dynamic again
Crystallization rolling, mixed crystal rolling, non-recrystallization rolling and static recovery, Static Recrystallization, complicated recrystallization and Recovery Process meeting
Cause the inhomogeneities of steel band crystal grain.And after reduction ratio is lifted, the Recrystallization nucleation point in steel band can be substantially improved, Yi Ji great
Measure high density Zona transformans（A large amount of nucleation points are provided for follow-up ferrite transformation）, when reduction ratio is more than 85%, sufficient ties again
Brilliant and phase transformation nucleation point, the influence of crystal grain inequality caused by significantly alleviating uneven microdeformation, realizes steel band crystal grain group
The fine and homogenization knitted.
Why batched in the present invention using Fast Cooling+medium temperature, be the granular bainite microstructure for obtaining fine, protect
Demonstrate,prove good comprehensive performance（High intensity, low yield strength ratio, performance uniformity, high tenacity etc.）.Pass through Fast Cooling to granular bayesian
Body phase transition temperature interval, can avoid high temperature ferrite transformation, form a large amount of polygonal ferrites, cause intensity insufficient, drop at the same time
Ferritic phase transition temperature in low granular bainite, and realize ferritic refinement, and suitable cooling rate and coiling temperature
Fine with achievable Ma Ao islands, improves the toughness of steel band.But cooling rate is preferably in convenient scope, when cooling rate is too low, iron element
Body is excessively thick；When cooling rate is excessive, steel strip surface and center portion cooling temperature difference are excessive, cause thickness direction tissue and hardness not
；Based on the composition design of product of the present invention, in conventional scope（2~7mm）, it is proposed that cooling rate works as thickness in 70~120 DEG C/s
, can be using opposite higher because thickness direction heat transfer is apart from short, steel strip surface and center portion temperature difference meeting smaller when relatively thin
Cooling rate, on the contrary thickness is more thick and solid, should use relatively low cooling rate.And suitable coiling temperature is at 500~600 DEG C, temperature mistake
Height can cause ferrite Ji Maao islands tissue thick, and the too low formation that can cause lath-shaped bainite structure of temperature, cause hard
Spend high and toughness reduction.
The thickness of slab microhardness fluctuation of the invention that why to demand perfection is less than 23HV1.0, is to ensure the uniform of steel band performance
Property.Its benefit is（1）Avoid causing stress raisers in deformation process because locally crossing hard spot in steel band, and then cause steel pipe mistake
Early failure；（2）Reduce the nonhomogeneous hardness of surface and center portion（Or performance difference）, avoid case hardness excessive and cause deformation to be opened
Split.
Why the present invention requires the yield tensile ratio of product to be less than 0.88, and elongation percentage is not less than 18%, is to ensure product
Plastic deformation ability.The product needs to be plastically deformed repeatedly in use, and yield tensile ratio is excessive and elongation percentage is too low, can lead
Cause steel pipe premature fatigue failures.
Compared with prior art, the present invention theoretical depth of implements reaches 7000m, actual grade at least than existing 3500 meters
At least 450 meters of increase, working pressure in well reaches 90MPa, and yield strength >=640MPa, tensile strength >=740MPa, yield tensile ratio is not
More than 0.88, elongation percentage A50mm（Tensile sample parallel portion width b=12.5mm）>=18%, section vickers hardness hv 1.0≤270 ,-
20 DEG C of low-temperature flexibilities are higher than 100J, and full thickness of slab hardness fluctuations are less than 23HV1.0；And the uniformity of hardness of product is good, toughness is excellent
Good, no surface copper brittleness is inclined to, and effectively improves the anti-fatigue performance of product.
Brief description of the drawings
Attached drawing 1 is metallographic structure figure of the invention.
Embodiment
The present invention is described in detail below：
Table 1 is various embodiments of the present invention and the comparative example of comparative example；
Table 2 is various embodiments of the present invention and the main technologic parameters list of comparative example；
Table 3 is various embodiments of the present invention and comparative example performance text list.
Various embodiments of the present invention are produced according to following steps：
1）Base is casting continuously to form after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to no more than 450
℃；
2）To heating strand, heating and temperature control keeps the temperature 60~90min at this temperature at 1260~1320 DEG C；
3）Roughing is carried out, rolling pass is 6 passages, and controls its end temp at 1050~1120 DEG C；
4）Finish rolling is carried out, and controls finishing temperature at 850~920 DEG C, finish rolling total reduction is not less than 85%；
5）Cooled down：Cooling velocity be 70~120 DEG C/s under be cooled to 550~650 DEG C, after be air-cooled to 500~600 DEG C again
Batched.
The composition value list of 1 various embodiments of the present invention of table and comparative example（wt%）
The main technologic parameters list of 2 various embodiments of the present invention of table and comparative example
3 various embodiments of the present invention of table and comparative example main performance detection statistics table
It can be analyzed from table 3, product possesses high intensity, its yield strength exists in more than 650MPa, tensile strength
More than 760MPa；Product yield tensile ratio is less than 0.88, and elongation percentage is higher than 18.5%, possesses good deformability；The impact of product
Work(is higher than 119J, good-toughness, and full thickness of slab hardness fluctuations are less than 23HV1.0.
Above-described embodiment is only the best example, and is not the restriction to embodiments of the present invention.
Claims (6)
1. a kind of CT100 grades of connecting pipes hot rolled strip, its component and weight percent content are：C：0.10~0.14%, Si：
0.10~0.30%, Mn：1.10~1.50%, P≤0.015%, S≤0.0020%, Cu：0.25~0.40%, Ni：0.15~
0.35%, Cr：0.60~1.00%, Nb：0.020~0.050%, V≤0.010%, Ti：0.010~0.030%, N≤0.0050%,
Al：0.015~0.060%, Ca：0.0008~0.0025%, surplus is Fe and is inevitably mingled with.
A kind of 2. CT100 grades of connecting pipes hot rolled strip as claimed in claim 1, it is characterised in that：The Cu weight percents
It is 0.28~0.36% than content.
A kind of 3. CT100 grades of connecting pipes hot rolled strip as claimed in claim 1, it is characterised in that：The Ni weight percents
It is 0.18~0.32% than content.
A kind of 4. CT100 grades of connecting pipes hot rolled strip as claimed in claim 1, it is characterised in that：The Cr weight percents
It is 0.65~0.93% than content.
A kind of 5. CT100 grades of connecting pipes hot rolled strip as claimed in claim 1, it is characterised in that：The Ca weight percents
It is 0.00092~0.002% than content.
6. a kind of production method of CT100 grades of connecting pipes hot rolled strip as claimed in claim 1, its step：
1）Base is casting continuously to form after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to no more than 450
℃；
2）To heating strand, heating and temperature control keeps the temperature 60~90min at this temperature at 1260~1320 DEG C；
3）Roughing is carried out, rolling pass is 6 passages, and controls its end temp at 1050~1120 DEG C；
4）Finish rolling is carried out, and controls finishing temperature at 850~920 DEG C, finish rolling total reduction is not less than 85%；
5）Cooled down：Cooling velocity be 70~120 DEG C/s under be cooled to 550~650 DEG C, after be air-cooled to 500~600 again
DEG C batched.
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| CN115254962A (en) * | 2022-08-18 | 2022-11-01 | 湖南华菱涟源钢铁有限公司 | Method for solving surface black spots of continuous casting and rolling short process line SPA-H |
| CN115386796A (en) * | 2022-08-15 | 2022-11-25 | 马鞍山钢铁股份有限公司 | Hot-rolled steel strip for CT 150-grade continuous oil pipe and production method thereof |
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| CN115386796A (en) * | 2022-08-15 | 2022-11-25 | 马鞍山钢铁股份有限公司 | Hot-rolled steel strip for CT 150-grade continuous oil pipe and production method thereof |
| CN115386796B (en) * | 2022-08-15 | 2023-03-03 | 马鞍山钢铁股份有限公司 | Hot-rolled steel strip for CT 150-grade continuous oil pipe and production method thereof |
| CN115254962A (en) * | 2022-08-18 | 2022-11-01 | 湖南华菱涟源钢铁有限公司 | Method for solving surface black spots of continuous casting and rolling short process line SPA-H |
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