CN108018488B - A kind of CT110 grades of connecting pipes hot rolled strip and production method - Google Patents
A kind of CT110 grades of connecting pipes hot rolled strip and production method Download PDFInfo
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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
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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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- 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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- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
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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
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- 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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Abstract
A kind of CT110 grades of connecting pipes hot rolled strip, component and wt%:C:0.11~0.15%, Si:0.10~0.30%, Mn:0.90~1.30%, 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%, Mo:0.10~0.30%, Ca:0.0008~0.0025%.Production stage: base is casting continuously to form after the processes such as converter smelting；Slab is heated；Roughing；Finish rolling；It cools down and batches.Theoretical depth of implements of the invention is up to 7600m, actual job depth rhinitis has at least 550 meters of technology increase, working pressure in well is up to 100 MPa, its yield strength >=680MPa, tensile strength >=780MPa, full plate thickness hardness fluctuations are less than 25HV1.0, yield tensile ratio less than 0.88, elongation percentage is not less than 17%, section vickers hardness hv 1.0≤280, -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 tube steel and production method, belong to a kind of yield strength >=680MPa, tensile strength >=
Uniform-full plate thickness hardness fluctuations of 780MPa, performance are less than 25HV1.0, yield tensile ratio and are not less than 17% less than 0.88, elongation percentage, reason
Reach 7600m by depth of implements, the High Strength Coiled Tubing with good deformability of working pressure in well up to 100MPa are used
Hot rolled strip and production method,.
Background technique
Continuous pipe is the novel tube for petroleum drilling and mining industry, is coiled in pipe 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 pipe dish again 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, at low cost
Advantage, but presently, there are its theoretical depth of implements to be no more than 6000 meters, the low deficiency of working pressure in well.
Before making the present invention, have:
The document that Chinese Patent Application No. is 201611162208.9, discloses a kind of " CT90 grades of connecting pipes hot-rolled steel
Band and its production method ", the product strength level is relatively low, in ultradeep well operation process, is difficult to bear big self weight,
And in operation process steel duct high pressure, with the continuous pipe of the production, theoretical depth of implements is only capable of reaching
6000m。
The document that Chinese Patent Application No. is 200710168545.3, disclose " a kind of steel for high-plasticity continuous oil pipe and
Its manufacturing method ", tissue in contain part ferrite and pearlite, 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 is in the presence of the possibility that copper brittleness occurs, easily induction fatigue crack, this can substantially
The fatigue life for reducing steel pipe is also unfavorable to underground work safely.
The document that Chinese Patent Application No. is 200810040895.6, disclose " a kind of CT90 cascade steel for continuous oil pipe and
Its manufacturing method ", intensity are equally insufficient for the needs of ultra-deep well operations；Contain higher V in its its ingredient design simultaneously,
This is unfavorable to the toughness and welding performance of product；Its steel plate yield tensile ratio is 0.90 or more, and deformability is poor, Wu Faman
The requirement being plastically deformed repeatedly is needed in such product operation process of foot.
Summary of the invention
It is an object of the invention to overcome deficiency present in above-mentioned document, a kind of depth of implements is provided and is increased than the prior art
Add hard up to 100 MPa, yield strength >=680MPa, tensile strength >=780MPa, full plate thickness not less than 550m, working pressure in well
Degree fluctuation be less than 25HV1.0, yield tensile ratio less than 0.88, elongation percentage be not less than 17%, section vickers hardness hv 1.0≤280, -20 DEG C
Low-temperature flexibility is higher than the CT110 grade connecting pipes hot rolled strip and production method of 100J.
Realize the measure of above-mentioned purpose:
A kind of CT110 grades of connecting pipes hot rolled strip, component and weight percent content are as follows: C:0.11~0.15%,
Si:0.10~0.30%, Mn:0.90~1.30%, 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%, Mo:0.10~0.30%, Ca:0.0008~0.0025%, surplus is for Fe and unavoidably
Be mingled with；And meet Mn+3.25Mo in 1.60 ~ 2.00% ranges；Metallographic structure is that average grain size is ultra-fine less than 2 μm
Granular bainite and volume ratio account for 5~15% ferrite bainites, and lath spacing is in 295 ~ 305nm.
Preferably: the Cu weight percent content is 0.28~0.36%.
Preferably: the Ni weight percent content is 0.18~0.32%.
Preferably: the Cr weight percent content is 0.65~0.93%.
Preferably: the Ca weight percent content is 0.00092~0.002%.
Preferably: the Mn+3.25Mo is in 1.66 ~ 1.95% ranges.
A kind of method for producing CT110 grades of connecting pipes hot rolled strip, step:
1) it is casting continuously to form base after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to being no more than
450℃；
2) slab is heated, heating and temperature control keeps the temperature 60~90min at 1260~1320 DEG C at this temperature；
3) roughing is carried out, rolling pass is 6 passages, and controls it and terminate temperature 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: being cooled to 520~620 DEG C in the case where cooling velocity is 50~100 DEG C/s, after be air-cooled to 470 again~
570 DEG C are batched.
The effect and mechanism of each element in the present invention
Carbon (C): most economical intensified element promotes the intensity of steel by gap solution strengthening.Increase carbon content, it can be substantially
The harden ability for promoting steel reduces the additional amount of other precious alloys, reduces production cost, while having to the yield tensile ratio for reducing steel
Benefit, therefore C content is unsuitable too low.But carbon content is higher, is more unfavorable for the low-temperature flexibility of steel, while easily being formed in steel grade tighter
The hard phase segregation band of weight, aggravates the structural heterogenity of steel, is unfavorable for the fatigue behaviour of product, therefore carbon content also can not mistake
It is high.The additive amount of convenient carbon is 0.11~0.15%.
Silicon (Si): mainly playing solution strengthening effect, is beneficial to assist desulfurization in smelting process, is also advantageous for promoting the tired of steel
Labor performance.But when 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 the surrender and tensile strength of steel.But manganese content is higher
When, such as inappropriate technology is also easy to produce more serious microstructure segregation, leads to ingredient, the tissue odds of steel.The additive amount of convenient manganese
It is 0.90~1.30%.
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
It fails with deformation, causes the performance of steel unstable, therefore the content of the phosphorus in steel, sulphur, nitrogen should be reduced as far as possible.
Copper, nickel (Cu, Ni): the intensity of steel can be promoted by solution strengthening, mainly rising in this copper improves the anti-corrosion weather-proof of steel
The effect of performance, general additional amount are 0.25% or more；Nickel can improve the red brittleness because copper is added, and general additional amount is copper content
2/3 or more.The weight percent content that preferably weight percent content of Cu is 0.28~0.36%, Ni is 0.18~
0.32%。
Chromium (Cr): the harden ability of steel is effectively promoted, 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
When too high levels, it is unfavorable for high-frequency resistance welding (HFRW) weldquality, easily formation flat spot, it is necessary to using welding protection, increase weldering
Connect difficulty and cost.The additive amount of convenient easy welding connecting pipes steel chromium is 0.60~1.00%.The weight hundred of preferably Cr
Dividing than content is 0.65~0.93%.
Niobium, titanium (Nb, Ti): micro alloying element can significantly refine crystal grain and play the role of precipitation strength, be remarkably improved
The austenite recrystallization temperature of steel expands Unhydrated cement range, is easy to implement high temperature controlled rolling, reduces mill load.But it is limited
It is designed in carbon content, when niobium, Ti content are excessively high, is not only difficult to play one's part to the full, while it is coarse not to may cause precipitation particle
Conducive to the toughness of steel.The additive amount of convenient niobium, titanium is respectively 0.020~0.050%, 0.010~0.030%.
Aluminium (Al): aluminium is main deoxidant element in steel, can significantly reduce the oxygen content in steel, while the knot of aluminium and nitrogen
Conjunction forms AlN, can effectively refine crystal grain.But when aluminium content is more than 0.06% in steel, easily lead to aluminium oxide be mingled with it is bright
It is aobvious to increase, the cleanliness of steel is reduced, it is unfavorable to the low-temperature flexibility of steel.The additive amount of convenient aluminium is respectively 0.015~
0.060%。
Calcium (Ca): carrying out Calcium treatment to steel during double refining, can improve the inclusion morphology in steel, improves steel
Impact flexibility, but excessive, the easy cleanliness for reducing steel is added, it is unfavorable to the low-temperature flexibility of steel.The additive amount of convenient calcium point
It Wei 0.0008~0.0025%.Preferably the weight percent content of Ca is 0.00092~0.002%.
Molybdenum (Mo): strong harden ability element, significantly postponement ferrite transformation inhibit the formation of ferrite and pearlite, so that
Steel obtains bainite structure rolling within the scope of the wider cooling rate of the latter.
In the present invention, very significantly (effect of molybdenum is more to effect of the harden ability with promotion intensity is promoted for molybdenum and manganese
Greatly).But to avoid molybdenum and manganese both element additive amounts are excessive and the problem that causes hardness exceeded, present invention combination molybdenum and manganese
Effect, therefore determines the additive amount of suitable molybdenum as an element combinations, and require Mn+3.25Mo should 1.60~
2.00%, preferably in 1.66 ~ 1.95% ranges.
In the present invention, why heating temperature is located at 1260~1320 DEG C and is carried out, and keep the temperature 60 at this temperature
~90min is to realize the homogenization of the easily segregation-alloy element such as Mn, Cr, improves the micro components segregation of steel billet, final improvement
The uniformity of the final microstructure of steel band.But when heating temperature is lower than 1260 DEG C, element microsegregation improvement is not significant,
Or too long soaking time is needed to realize the diffusion-homogenization of alloying element, it is greatly reduced so as to cause production efficiency；And
As heating temperature increases, austenite grain is gradually roughened, when heating temperature is higher than 1320 DEG C (or heating temperature is higher than
1300 DEG C, but when heating and thermal insulation overlong time), austenite grain is excessively roughened, and leads to final products coarse grains and surrender
Intensity is insufficient.Therefore, convenient heating temperature is at 1260~1320 DEG C, preferred heating temperature at 1260~1300 DEG C,
Soaking time is in 60~90min.
Total reduction >=85% that finish rolling why is set in the present invention, be realize steel band tissue fine and uniformly
Change.It is 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 relatively high, to subtract
Few rolling load, and then guarantee smoothly to produce.But when final rolling temperature is higher, will lead to steel band finishing stands include dynamic again
Crystallization rolling, mixed crystal rolling, non-recrystallization rolling and static recovery, Static Recrystallization, complicated recrystallization and Recovery Process meeting
Lead to the inhomogeneities of steel band crystal grain.And after reduction ratio is promoted, the Recrystallization nucleation point in steel band can be substantially improved, Yi Ji great
It measures high density Zona transformans (providing a large amount of nucleation points for subsequent ferrite transformation), when reduction ratio is more than 85%, sufficient ties again
Brilliant and phase transformation nucleation point, substantially alleviates the influence of the unevenness of crystal grain caused by uneven microdeformation, realizes steel band crystal grain group
The fine and homogenization knitted.
Why batched using Fast Cooling+middle low temperature in the present invention, be to obtain the granular bainite microstructure of fine,
Guarantee good comprehensive performance (high intensity, low yield strength ratio, performance uniformity, high tenacity etc.).Pass through Fast Cooling to granular shellfish
Family name's body phase transition temperature interval can avoid high temperature ferrite transformation, form a large amount of polygonal ferrites, cause intensity insufficient, simultaneously
Ferritic phase transition temperature in granular bainite is reduced, and realizes ferritic refinement, and suitable cooling rate and coiling temperature
The fine that the island Ma Ao can be achieved is matched, the toughness of steel band is improved.But cooling rate is preferably in convenient range, when cooling rate is too low, iron
Ferritic is excessively coarse；When cooling rate is excessively high, steel strip surface and center portion cooling temperature difference are excessive, lead to thickness direction tissue and hardness
It is uneven；Ingredient design based on product of the present invention, in conventional range (2~7mm), it is proposed that cooling rate works as thickness in 50~100 DEG C/s
When spending relatively thin, because thickness direction heat transfer is apart from short, steel strip surface and center portion temperature difference can be smaller, can use relatively higher
Cooling rate should use relatively low cooling rate otherwise thickness is more thick and solid.And suitable coiling temperature is at 470~570 DEG C, temperature
It is excessively high to will lead to the island ferrite Ji Maao organizational coarseness, and the too low formation that will lead to excessive lath-shaped bainite structure of temperature,
Lead to being greatly reduced for excessive high hardness and toughness.
Why the present invention will demand perfection the fluctuation of plate thickness microhardness less than 20HV1.0, be to guarantee the uniform of steel band performance
Property.Its benefit is that (1) avoids leading to stress raisers in deformation process because locally crossing hard spot in steel band, and then leads to steel pipe mistake
Early failure；(2) nonhomogeneous hardness (or performance difference) for reducing surface and center portion, avoids surface hardness excessively high and deformation is caused to be opened
It splits.
Why the present invention requires the yield tensile ratio of product lower than 0.88, and elongation percentage is not less than 17%, is to guarantee product
Plastic deformation ability.The product needs to be plastically deformed repeatedly in use, and yield tensile ratio is excessively high 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, up to 7600m, actual job depth increases than the prior art
At least 550 meters, working pressure in well is up to 100 MPa, yield strength >=680MPa, tensile strength >=780MPa, full plate thickness hardness
Fluctuation is less than 25HV1.0, and yield tensile ratio is less than 0.88, and elongation percentage is not less than 17%, section vickers hardness hv 1.0≤280, and -20 DEG C low
Warm toughness is higher than 100J, and is inclined to without surface copper brittleness, effectively improves the anti-fatigue performance of product.
Detailed description of the invention
Fig. 1 is 5000 times of tissue topographies of the invention；
Fig. 2 is middle plate strip Bainite Morphology of the present invention.
Specific embodiment
The present invention is described in detail below:
Table 1 is the comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example；
Table 3 is various embodiments of the present invention and comparative example performance text list.
Various embodiments of the present invention produce according to the following steps:
1) it is casting continuously to form base after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to being no more than
450℃；
2) slab is heated, heating and temperature control keeps the temperature 60~90min at 1260~1320 DEG C at this temperature；
3) roughing is carried out, rolling pass is 6 passages, and controls it and terminate temperature 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: being cooled to 520~620 DEG C in the case where cooling velocity is 50~100 DEG C/s, after be air-cooled to 470 again~
570 DEG C are batched.
The composition value list (wt%) of 1 various embodiments of the present invention of table and comparative example
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 analyze out from table 3, product has high intensity, and in 692MPa or more, tensile strength exists yield strength
811MPa or more；Product yield tensile ratio is lower than 0.88, and elongation percentage is higher than 17.5%, has good deformability；The impact of product
Function is higher than 109J, and good-toughness, Vickers hardness, full plate hardness fluctuations are no more than 25HV1.0.
Above-described embodiment is only the best example, rather than a limitation of the embodiments of the present invention.
Claims (7)
1. a kind of CT110 grades of connecting pipes hot rolled strip, component and weight percent content are as follows: C:0.11~0.15%, Si:
0.10~0.30%, Mn:0.90~1.30%, 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%, Mo:0.10~0.30%, Ca:0.0008~0.0025%, surplus is for Fe and unavoidably
Be mingled with；And meet Mn+3.25Mo in 1.60 ~ 2.00% ranges；Metallographic structure is ultra-fine granular bainite, average crystalline substance
Particle size is less than 2 μm, volume ratio 85 ~ 95%；A small amount of ferrite bainite and its volume ratio account for 5~15%, and lath is spaced about
300nm；Production method:
1) it is casting continuously to form base after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to being no more than 450
℃；
2) slab is heated, heating and temperature control keeps the temperature 60~90min at 1260~1320 DEG C at this temperature；
3) roughing is carried out, rolling pass is 6 passages, and controls it and terminate temperature 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 50~100 DEG C/s under be cooled to 520~620 DEG C, after be air-cooled to 470~570 DEG C again
It is batched.
2. a kind of CT110 grades of connecting pipes hot rolled strip as described in claim 1, it is characterised in that: the Cu weight percent
It is 0.28~0.36% than content.
3. a kind of CT110 grades of connecting pipes hot rolled strip as described in claim 1, it is characterised in that: the Ni weight percent
It is 0.18~0.32% than content.
4. a kind of CT110 grades of connecting pipes hot rolled strip as described in claim 1, it is characterised in that: the Cr weight percent
It is 0.65~0.93% than content.
5. a kind of CT110 grades of connecting pipes hot rolled strip as described in claim 1, it is characterised in that: the Ca weight percent
It is 0.00092~0.002% than content.
6. a kind of CT110 grades of connecting pipes hot rolled strip as described in claim 1, it is characterised in that: the Mn+3.25Mo exists
In 1.66 ~ 1.95% ranges.
7. producing a kind of method of CT110 grades of connecting pipes hot rolled strip as described in claim 1, step:
1) it is casting continuously to form base after converter, argon station, ladle furnace, vacuum drying oven, Calcium treatment, and by casting blank stacking slow cooling to being no more than 450
℃；
2) slab is heated, heating and temperature control keeps the temperature 60~90min at 1260~1320 DEG C at this temperature；
3) roughing is carried out, rolling pass is 6 passages, and controls it and terminate temperature 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 50~100 DEG C/s under be cooled to 520~620 DEG C, after be air-cooled to 470~570 DEG C again
It is batched.
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| CN113637925B (en) * | 2020-04-27 | 2022-07-19 | 宝山钢铁股份有限公司 | Steel for quenched and tempered continuous oil pipe, hot-rolled steel strip, steel pipe and manufacturing method thereof |
| CN111690801B (en) * | 2020-05-25 | 2021-11-02 | 中天钢铁集团有限公司 | Production process of alloy tool steel wire rod for obtaining full bainite structure |
| 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 |
| CN115537674A (en) * | 2022-09-02 | 2022-12-30 | 杰森能源技术有限公司 | On-line production continuous quenching and tempering high-performance coiled tubing and manufacturing method thereof |
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| JPH10237551A (en) * | 1997-02-25 | 1998-09-08 | Nkk Corp | Production of hot rolled steel sheet excellent in fatigue characteristic and stretch-flanging property |
| US20060060267A1 (en) * | 2004-09-17 | 2006-03-23 | Benson Dan T | Method for extending the life of thin walled tubing and austempered weld stress relieved thin walled tubing |
| JP2007107032A (en) * | 2005-10-12 | 2007-04-26 | Nisshin Steel Co Ltd | Method for producing steel pipe for hollow stabilizer, and producing method for producing hollow stabilizer |
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| KR101257161B1 (en) * | 2011-01-28 | 2013-04-22 | 현대제철 주식회사 | Hot-rolled steel sheet, method of manufacturing the hot-rolled steel sheet and method of manufacturing oil tubular country goods using the hot-rolled steel sheet |
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