CN109182914A - Low hammer temperature X70 pipe line steel of one kind and preparation method thereof - Google Patents
Low hammer temperature X70 pipe line steel of one kind and preparation method thereof Download PDFInfo
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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
- C22C38/02—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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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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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- 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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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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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
- C21D2211/005—Ferrite
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Abstract
The present invention provides low hammer temperature X70 pipe line steel of one kind and preparation method thereof, wherein the low hammer temperature X70 pipe line steel includes following chemical component and mass percent are as follows: C:0.04~0.07%, Si:0.15~0.26%, Mn:1.45~1.65%, P≤0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N≤0.004%, O≤0.004%, H≤0.0002%.The low hammer temperature X70 pipe line steel that the present invention obtains (- 50~-30 DEG C) toughness with higher and lear energy at a lower temperature, have broad application prospects.
Description
Technical field
The invention belongs to metallurgical material technical fields, especially pipe line steel field, and in particular to a kind of low hammer temperature X70
Pipe line steel and preparation method thereof.
Background technique
In recent years, with the further exploitation of petroleum, natural gas and other energy, the demand of pipe line steel increasingly increases,
The exploitation and production of pipe line steel are rapidly developed.But petroleum, natural gas and other energy extraction areas are generally in remote districts, ring
Border is more severe, transports industry prosperity area distance, and geomorphological structure is complicated, and service condition is worsening, especially in recent years
Come, the U.S. pass through alaskan pipeline, Russian West Siberia-center gas transmission line, Russian Far East pipeline construction, in
All in Frozen Ground Area and extremely frigid zones, Service Environment temperature is -20 DEG C for sub- pipeline, the second west to east gas pipeline project and northern pipeline construction
~-70 DEG C, this requires conveyance conduits to have excellent low-temperature impact toughness, just can guarantee pipe safety.Therefore severe cold area
Petroleum Production base, higher requirement is proposed to the low-temperature flexibility of conveying material, low-temperature flexibility is that can material be on active service safely
An important indicator.
Modified test method of the v-notch drop hammer test (DWTT) as standard press notch drop hammer test,
The resistance that sample extends ductility crack can be more preferably evaluated when for high tenacity pipe line steel, in high grade pipe line steel production process
In, intensity index is easier to reach, but for toughness index, especially block hammer performance, affected by various factors, qualification rate is inclined
It is low, cause that the production cost increases.Therefore, it is imperative to improve block hammer performance, reduces business economic loss, while it is defeated to improve pipeline
The safety sent.
Currently, the production work of X70 pipe line steel is described in Zheng et al. in " production practices of the high NbX70 pipe line steel of this steel "
Skill, chemical component, mechanical property, impact flexibility, block hammer performance etc. wherein test steel is free of Mo, and heat in the publication
Furnace temperature is higher and temperature of dropping hammer is -15 DEG C, and obtained pipe line steel is difficult to apply to the more severe area of environment as conveying
Tubing.Week rare cloud also described in " exploitation of Taiyuan Iron and Steel Co. X70 high-grade pipe line steel " production technology of X70 pipe line steel, chemistry at
Point, mechanical property, impact flexibility, block hammer performance etc., but the temperature of dropping hammer of gained test steel is also only -15 DEG C in the publication,
It is not able to satisfy production needs.Qin Liguo describes a kind of production of X70 pipe line steel in " exploitation and production of Pipeline Steel Plate X70 "
Technique, chemical component, mechanical property, impact flexibility, block hammer performance etc., but the temperature of dropping hammer of the pipe line steel obtained according to the document
- 5 DEG C are also only, the needs of actual production can not be met.
The content of background technology part is only the technology that inventor is known, not the existing skill of natural representative this field
Art.
Summary of the invention
For the prior art, there are one or more of problems, and in one aspect of the invention, the present invention provides one kind
Low hammer temperature X70 pipe line steel, the chemical component and mass percent of the pipe line steel are as follows: C:0.04~0.07%, Si:0.15
~0.26%, Mn:1.45~1.65%, P≤0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~
0.020%, Cr:0.20~0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N
≤ 0.004%, O≤0.004%, H≤0.0002%, remaining is iron and other inevitable impurity.
Preferably, above-mentioned pipe line steel chemical component and mass percent are as follows: C:0.055%, Si:0.205%, Mn:
1.55%, P:0.010%, S:0.004%, Nb:0.060%, Ti:0.015%, Cr:0.30%, Ni:0.20%, Mo:
0.30%, Alt:0.035%, N:0.0030%, O:0.0018%, H:0.00013%, remaining is inevitable with other for iron
Impurity.
Preferably, above-mentioned pipe line steel is in DWTT test, when test temperature is -50~-30 DEG C, the individual sample section of shear
>=80%, two sample section of shear average value >=85%.
Preferably, the microscopic structure of the pipe line steel is based on acicular ferrite.
In another aspect of this invention, the present invention provides the preparation method of above-mentioned low hammer temperature X70 pipe line steel, institutes
State method comprising steps of molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling, control cooling, wherein the molten iron is pre-
Processing includes desulfurization, decarburization, dephosphorization treatment；It includes converter smelting, external refining, RH furnace vacuum outgas that the step, which is smelted,；Institute
Slab is obtained after stating continuous casting step, the slab includes the chemical component of following mass percent: C:0.04~0.07%, Si:
0.15~0.26%, Mn:1.45~1.65%, P≤0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~
0.020%, Cr:0.20~0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N
≤ 0.004%, O≤0.004%, H≤0.0002%.
Preferably, above-mentioned steps slab heating temperature is 1170 DEG C~1200 DEG C.
Preferably, above-mentioned controlled rolling step includes roughing and finish rolling, wherein the roughing start rolling temperature be 1110 DEG C~
1150 DEG C, finishing temperature is 980 DEG C~1050 DEG C, and single pass reduction ratio >=11% accumulates reduction ratio >=61%, to the roughing
The finish rolling, finish rolling start rolling temperature≤950 DEG C, single pass pressure are carried out when afterwards with a thickness of 2.6~3.4 times of finished product thickness
Rate >=15%, accumulates reduction ratio >=65%, and finishing temperature is 830 DEG C~860 DEG C.
Preferably, above-mentioned control is cooling cooling using ACC, and the cooling group number is 6~10 groups, with the cold of 13~20 DEG C/s
But rate is cooled to 460~520 DEG C.
According to above scheme, method of the invention is to use continuous casting billet for hot rolling raw material, is heated, controlled rolling and controlled cooling, most
A kind of X70 pipe line steel with superior low-temperature block hammer performance is obtained eventually.Microscopic structure after the pipe line steel controlled rolling and controlled cooling is with needle-shaped
Based on ferrite, toughness with higher and lear energy can effectively prevent the explosion of pipe line steel.And it is torn by dropping hammer
Splitting test (DWTT) proves: when test temperature is -50~-30 DEG C, X70 pipe line steel individual sample shear surface that the present invention obtains
Product >=80%, two sample section of shear average value >=85%, it was demonstrated that the X70 pipe line steel that the present invention obtains is at a lower temperature
(- 50~-30 DEG C) all have higher toughness and lear energy, may be used as the tubing under low temperature environment, have wide
Application prospect.
Detailed description of the invention
Attached drawing is used to provide further understanding of the present invention, and constitutes part of specification, with reality of the invention
It applies example to be used to explain the present invention together, not be construed as limiting the invention.In the accompanying drawings:
Fig. 1 is the microstructure picture on the Pipeline Steel Plate surface obtained of the embodiment of the present invention 1；
Fig. 2 is the microstructure picture at 1/2 section of Pipeline Steel Plate obtained of the embodiment of the present invention 1；
Fig. 3 is the microstructure picture at 1/4 section of Pipeline Steel Plate obtained of the embodiment of the present invention 1.
Specific embodiment
Hereinafter, certain exemplary embodiments are simply just described.As one skilled in the art will recognize that
Like that, without departing from the spirit or scope of the present invention, described embodiment can be modified by various different modes.
Therefore, attached drawing and description are considered essentially illustrative rather than restrictive.
Hereinafter, preferred embodiments of the present invention will be described with reference to the accompanying drawings, it should be understood that preferred reality described herein
Apply example only for the purpose of illustrating and explaining the present invention and is not intended to limit the present invention.
In order to resolve at least one or more of the problems as set forth in the prior art, the object of the present invention is to provide one kind with low
The X70 pipe line steel for hammering temperature into shape, it is a further object of the present invention to provide a kind of preparation sides of X70 pipe line steel with low hammer temperature
Method.
The purpose of the present invention is realized by following specific embodiments:
In the first embodiment of the present invention, the present invention provides a kind of low hammer temperature X70 pipe line steel, the pipe line steel
Chemical component and mass percent are as follows: C:0.04~0.07%, Si:0.15~0.26%, Mn:1.45~1.65%, P≤
0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, Ni:0.15
~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N≤0.004%, O≤0.004%, H≤
0.0002%, remaining is iron and other inevitable impurity.Such as the chemical component and mass percent of the pipe line steel can
With are as follows: C:0.04%, Si:0.26%, Mn:1.45%, P:0.012%, S:0.007%, Nb:0.08%, Ti:0.010%,
Cr:0.40%, Ni:0.15%, Mo:0.40%, Alt:0.020%, N:0.004%, O:0.004%, H:0.0002%, remaining
For iron and other inevitable impurity；Or C:0.07%, Si:0.15%, Mn:1.65%, P:0.010%, S:0.005%,
Nb:0.04%, Ti:0.020%, Cr:0.20%, Ni:0.25%, Mo:0.20%, Alt:0.050%, N:0.003%, O:
0.00:3%, H:0.0002%, remaining is iron and other inevitable impurity；Or C:0.05%, Si:0.20%, Mn:
1.55%, P:0.012%, S:0.007%, Nb:0.06%, Ti:0.015%, Cr:0.23%, Ni:0.20%, Mo:
0.30%, Alt:0.035%, N:0.004%, O:0.004%, H:0.0002%, remaining is inevitably miscellaneous with other for iron
Matter；Deng.
In one preferred embodiment, the chemical component and mass percent of above-mentioned pipe line steel are as follows: C:0.055%,
Si:0.205%, Mn:1.55%, P:0.010%, S:0.004%, Nb:0.060%, Ti:0.015%, Cr:0.30%, Ni:
0.20%, Mo:0.30%, Alt:0.035%, N:0.0030%, O:0.0018%, H:0.00013%, remaining is iron and other
Inevitable impurity.
In one preferred embodiment, above-mentioned pipe line steel is in DWTT test, when test temperature is -50~-30 DEG C,
Individual sample section of shear >=80%, two sample section of shear average value >=85%.
In one preferred embodiment, the microscopic structure of above-mentioned pipe line steel is based on acicular ferrite.
In second embodiment of the present invention, the present invention provides the preparation side of above-mentioned low hammer temperature X70 pipe line steel
Method, the method includes the steps: molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling, control cooling；Concrete operations
Method are as follows: progress desulfurizing iron pretreatment first carries out LF external refining and RH using top and bottom combined blown converter decarburization, dephosphorization
Furnace vacuum outgas, sheet billet continuous casting (in electromagnetic agitation, slighter compress) obtain slab, are cleared up slab, slow cooling and quality examination.
The slab includes the chemical component of following mass percent: C:0.04~0.07%, Si:0.15~0.26%, Mn:1.45~
1.65%, P≤0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~0.020%, Cr:0.20~
0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N≤0.004%, O≤
0.004%, H≤0.0002%.Such as comprising chemical component and mass percent can be with are as follows: C:0.04%, Si:0.26%,
Mn:1.45%, P:0.012%, S:0.007%, Nb:0.08%, Ti:0.010%, Cr:0.40%, Ni:0.15%, Mo:
0.40%, Alt:0.020%, N:0.004%, O:0.004%, H:0.0002%；Or C:0.07%, Si:0.15%, Mn:
1.65%, P:0.010%, S:0.005%, Nb:0.04%, Ti:0.020%, Cr:0.20%, Ni:0.25%, Mo:
0.20%, Alt:0.050%, N:0.003%, O:0.00:3%, H:0.0002%；Or C:0.05%, Si:0.20%, Mn:
1.55%, P:0.012%, S:0.007%, Nb:0.06%, Ti:0.015%, Cr:0.23%, Ni:0.20%, Mo:
0.30%, Alt:0.035%, N:0.004%, O:0.004%, H:0.0002%；Deng.Then slab is heated, is heated
It is 1170 DEG C~1200 DEG C to temperature to come out of the stove.It is rolled after high-pressure water descaling, rolling includes roughing and finish rolling；Wherein roughing is opened
1110 DEG C~1150 DEG C of temperature are rolled, 980 DEG C~1050 DEG C of finishing temperature, guarantees single pass reduction ratio >=11%, accumulates reduction ratio
>=61%, finish rolling is carried out when after roughing with a thickness of 2.6~3.4 times of finished product thickness, finish rolling start rolling temperature≤950 DEG C guarantee
Single pass reduction ratio >=15% accumulates reduction ratio >=65%, and finishing temperature range is 830 DEG C~860 DEG C, by ACC after finish rolling
Cooling, cooling 6~10 groups of number of group is cooled to 460~520 DEG C with the cooling rate of 13~20 DEG C/s, is sent to straightener aligning.
Below with reference to embodiment, the present invention is described in further detail, and embodiments of the present invention are not limited thereto.
Embodiment 1: the preparation of low hammer temperature X70 pipe line steel of the invention
Molten iron pretreatment is smelted, continuous casting: molten iron carries out desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization, into
Row LF external refining and RH furnace vacuum outgas, sheet billet continuous casting (electromagnetic agitation, slighter compress) obtain slab, carry out to slab clear
Reason, slow cooling, quality examination.
The chemical component of gained slab is as shown in table 1 below:
Table 1: Chemical Composition in Cast Billet and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | Ni | Mo | Ti | Cr | O | N | H |
| 0.040 | 0.15 | 1.45 | 0.008 | 0.003 | 0.020 | 0.040 | 0.15 | 0.20 | 0.010 | 0.20 | 0.0021 | 0.0026 | 0.00012 |
Slab heating, controlled rolling, control cooling: slab is heated to 1170 DEG C and is come out of the stove, is rolled after high-pressure water descaling
System, 980 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=11%, accumulates reduction ratio 62% by 1110 DEG C of roughing start rolling temperature,
To 2.6 times with a thickness of finished product thickness, 930 DEG C of finish rolling start rolling temperature, the two-stage guarantees that single pass reduction ratio is >=15%, accumulation
Reduction ratio 66%, finishing temperature is 840 DEG C, cooling by ACC after finish rolling, cooling 7 groups of number of group, with the cooling rate of 13 DEG C/s after finish rolling
460 DEG C are cooled to, straightener aligning is sent to.As Fig. 1,2 and 3 show the table for the X70 Pipeline Steel Plate that embodiment 1 obtains
Microstructure picture at face, the 1/2 section section Chu He1/4, it is micro- after the pipe line steel controlled rolling and controlled cooling as we can see from the figure
Tissue is based on acicular ferrite.Due to dislocation density with higher inside acicular ferrite, the height of dislocation density is to determine
An important factor for determining steel obdurability, therefore, Fig. 1,2 and 3 also demonstrate what the embodiment of the present invention obtained from microstructure
X70 pipe line steel has more high-strength toughness.
DWTT test: at -30 DEG C of test temperature, experimental result is as shown in table 2 below, the individual sample section of shear >=80%,
Two sample section of shear average values are 96%, show X70 pipe line steel that the embodiment is prepared at -30 DEG C of test temperature
Toughness with higher and lear energy.
Table 2:DWTT test result
Embodiment 2: the preparation of low hammer temperature X70 pipe line steel of the invention
Molten iron pretreatment is smelted, continuous casting: molten iron carries out desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization, into
Row LF external refining and RH furnace vacuum outgas, sheet billet continuous casting (electromagnetic agitation, slighter compress) obtain slab, carry out to slab clear
Reason, slow cooling, quality examination.
The chemical component of gained slab is as shown in table 3 below:
Table 3: Chemical Composition in Cast Billet and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | Ni | Mo | Ti | Cr | O | N | H |
| 0.055 | 0.205 | 1.55 | 0.010 | 0.004 | 0.035 | 0.060 | 0.20 | 0.30 | 0.015 | 0.30 | 0.0018 | 0.0030 | 0.00013 |
Slab heating, controlled rolling, control cooling: slab is heated to 1185 DEG C and is come out of the stove, is rolled after high-pressure water descaling
System, 1015 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=11%, accumulates reduction ratio 63% by 1130 DEG C of roughing start rolling temperature,
To 3.0 times with a thickness of finished product thickness, 930 DEG C of finish rolling start rolling temperature, the two-stage guarantees that single pass reduction ratio is >=15%, accumulation
Reduction ratio 67%, finishing temperature is 860 DEG C, cooling by ACC after finish rolling, cooling 8 groups of number of group, with the cold of 16.5 DEG C/s after finish rolling
Speed is cooled to 490 DEG C, is sent to straightener aligning.
DWTT test: when -40 DEG C of test temperature, experimental result is shown in the following table 4, individual sample sections of shear >=80%, two
A sample section of shear average value is 93.5%, shows X70 pipe line steel that the embodiment is prepared at -40 DEG C of test temperature
Toughness with higher and lear energy.
4 DWTT test result of table
Embodiment 3: the preparation of low hammer temperature X70 pipe line steel of the invention
Molten iron pretreatment is smelted, continuous casting: molten iron carries out desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization, into
Row LF external refining and RH furnace vacuum outgas, sheet billet continuous casting (electromagnetic agitation, slighter compress) obtain slab, carry out to slab clear
Reason, slow cooling, quality examination.
The chemical component of gained slab is as shown in table 5 below:
Table 5: Chemical Composition in Cast Billet and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | Ni | Mo | Ti | Cr | O | N | H |
| 0.070 | 0.26 | 1.65 | 0.012 | 0.007 | 0.050 | 0.080 | 0.20 | 0.40 | 0.020 | 0.40 | 0.0015 | 0.0029 | 0.00011 |
Slab heating, controlled rolling, control cooling: slab is heated to 1200 DEG C and is come out of the stove, is rolled after high-pressure water descaling
System, 1050 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=11%, accumulates reduction ratio 63% by 1150 DEG C of roughing start rolling temperature,
To 3.4 times with a thickness of finished product thickness, 930 DEG C of finish rolling start rolling temperature, the two-stage guarantees that single pass reduction ratio is >=15%, accumulation
Reduction ratio 68%, finishing temperature is 845 DEG C, cooling by ACC after finish rolling, cooling 10 groups of number of group, with the cold of 20 DEG C/s after finish rolling
Speed is cooled to 520 DEG C, is sent to straightener aligning.
DWTT test: when -50 DEG C of test temperature, experimental result is shown in the following table 6, individual sample sections of shear >=80%, two
A sample section of shear average value is 91%, and the X70 pipe line steel for showing that the embodiment is prepared has at -50 DEG C of test temperature
There are higher toughness and lear energy.
6 DWTT test result of table
Finally, it should be noted that the foregoing is only a preferred embodiment of the present invention, it is not intended to restrict the invention,
Although the present invention is described in detail referring to the foregoing embodiments, for those skilled in the art, still may be used
To modify the technical solutions described in the foregoing embodiments or equivalent replacement of some of the technical features.
All within the spirits and principles of the present invention, any modification, equivalent replacement, improvement and so on should be included in of the invention
Within protection scope.
Claims (8)
1. a kind of low hammer temperature X70 pipe line steel, which is characterized in that the chemical component and mass percent of the pipe line steel are as follows:
C:0.04~0.07%, Si:0.15~0.26%, Mn:1.45~1.65%, P≤0.012%, S≤0.007%, Nb:0.04
~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%,
Alt:0.020~0.050%, N≤0.004%, O≤0.004%, H≤0.0002%, remaining is inevitable with other for iron
Impurity.
2. low hammer temperature X70 pipe line steel described in claim 1, which is characterized in that the chemical component and matter of the pipe line steel
Measure percentage are as follows: C:0.055%, Si:0.205%, Mn:1.55%, P:0.010%, S:0.004%, Nb:0.060%, Ti:
0.015%, Cr:0.30%, Ni:0.20%, Mo:0.30%, Alt:0.035%, N:0.0030%, O:0.0018%, H:
0.00013%, remaining is iron and other inevitable impurity.
3. low hammer temperature X70 pipe line steel of any of claims 1 or 2, which is characterized in that the pipe line steel is tested in DWTT
In, when test temperature is -50~-30 DEG C, individual sample section of shear >=80%, two sample section of shear average value >=
85%.
4. low hammer temperature X70 pipe line steel of any of claims 1 or 2, which is characterized in that the microscopic structure of the pipe line steel with
Based on acicular ferrite.
5. the preparation method of low hammer temperature X70 pipe line steel of any of claims 1-4, which is characterized in that described
Method comprising steps of molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling, control cooling, wherein the molten iron is located in advance
Reason includes desulfurization, decarburization, dephosphorization treatment；It includes converter smelting, external refining, RH furnace vacuum outgas that the step, which is smelted,；It is described
Slab is obtained after continuous casting step, the slab includes the chemical component of following mass percent: C:0.04~0.07%, Si:
0.15~0.26%, Mn:1.45~1.65%, P≤0.012%, S≤0.007%, Nb:0.04~0.08%, Ti:0.010~
0.020%, Cr:0.20~0.40%, Ni:0.15~0.25%, Mo:0.20~0.40%, Alt:0.020~0.050%, N
≤ 0.004%, O≤0.004%, H≤0.0002%.
6. the preparation method of low hammer temperature X70 pipe line steel described in claim 5, which is characterized in that the step slab adds
Hot temperature is 1170 DEG C~1200 DEG C.
7. the preparation method of low hammer temperature X70 pipe line steel described in claim 5, which is characterized in that the controlled rolling step
It suddenly include roughing and finish rolling, wherein the roughing start rolling temperature is 1110 DEG C~1150 DEG C, finishing temperature is 980 DEG C~1050
DEG C, single pass reduction ratio >=11% accumulates reduction ratio >=61%, with a thickness of 2.6~3.4 times of finished product thickness after the roughing
Finish rolling described in Shi Jinhang, finish rolling start rolling temperature≤950 DEG C, single pass reduction ratio >=15% accumulate reduction ratio >=65%, eventually
Rolling temperature is 830 DEG C~860 DEG C.
8. the preparation method of low hammer temperature X70 pipe line steel described in claim 5, which is characterized in that the control cooling is adopted
Cooling with ACC, the cooling group number is 6~10 groups, is cooled to 460~520 DEG C with the cooling rate of 13~20 DEG C/s.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111020408A (en) * | 2019-12-31 | 2020-04-17 | 包头钢铁（集团）有限责任公司 | Thick-specification low-temperature-resistant and tough hot-rolled steel strip for natural gas conveying pipe and preparation method thereof |
| CN111057954A (en) * | 2020-01-02 | 2020-04-24 | 鞍钢股份有限公司 | High-strength pipeline rolled plate for large thick wall acidity and manufacturing method thereof |
| CN111122009A (en) * | 2019-12-16 | 2020-05-08 | 中国石油天然气集团有限公司 | Method for determining test temperature of DWTT (DWTT) thinning sample of pipeline steel |
| CN114178414A (en) * | 2021-11-16 | 2022-03-15 | 山东钢铁集团日照有限公司 | Method for improving flatness of X70M pipeline steel plate through secondary straightening |
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| CN107604259A (en) * | 2017-08-31 | 2018-01-19 | 包头钢铁（集团）有限责任公司 | A kind of X70 line steel hot rollings coiled sheet and its production method |
| CN108546885A (en) * | 2018-07-03 | 2018-09-18 | 鞍钢股份有限公司 | A kind of the L555M pipe line steels and its manufacturing method of excellent in low temperature toughness |
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| CN107604259A (en) * | 2017-08-31 | 2018-01-19 | 包头钢铁（集团）有限责任公司 | A kind of X70 line steel hot rollings coiled sheet and its production method |
| CN108546885A (en) * | 2018-07-03 | 2018-09-18 | 鞍钢股份有限公司 | A kind of the L555M pipe line steels and its manufacturing method of excellent in low temperature toughness |
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| CN111122009A (en) * | 2019-12-16 | 2020-05-08 | 中国石油天然气集团有限公司 | Method for determining test temperature of DWTT (DWTT) thinning sample of pipeline steel |
| CN111020408A (en) * | 2019-12-31 | 2020-04-17 | 包头钢铁（集团）有限责任公司 | Thick-specification low-temperature-resistant and tough hot-rolled steel strip for natural gas conveying pipe and preparation method thereof |
| CN111057954A (en) * | 2020-01-02 | 2020-04-24 | 鞍钢股份有限公司 | High-strength pipeline rolled plate for large thick wall acidity and manufacturing method thereof |
| CN114178414A (en) * | 2021-11-16 | 2022-03-15 | 山东钢铁集团日照有限公司 | Method for improving flatness of X70M pipeline steel plate through secondary straightening |
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