CN109234633A - A kind of low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment and preparation method thereof - Google Patents
A kind of low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment and preparation method thereof Download PDFInfo
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- CN109234633A CN109234633A CN201811267463.9A CN201811267463A CN109234633A CN 109234633 A CN109234633 A CN 109234633A CN 201811267463 A CN201811267463 A CN 201811267463A CN 109234633 A CN109234633 A CN 109234633A
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
- C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
- C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
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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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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—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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- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D2211/004—Dispersions; Precipitations
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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
Abstract
The present invention provides a kind of low preheating temperature 690MPa grades of high strength steel plates and preparation method thereof of rare earth treatment, wherein the steel plate includes chemical component and mass percent are as follows: C:0.09~0.15%, Si:0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤0.010%, Nb:0.04~0.08%, V:0.05~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤0.030%, Alt:0.020~0.050%, N≤0.005%, O≤0.004%.The 690MPa grade high strength steel plate that the present invention obtains is added rare earth but Ni, Mo is not added and has low preheating temperature, reduce costs and improves comprehensive mechanical property by rare earth treatment, extends service life, with good economic efficiency.
Description
Technical field
The invention belongs to metallurgical material technical field, especially high-strength engineering machinery rings domains, and in particular to a kind of
Low preheating temperature 690MPa grades of high-strength steel of rare earth treatment and preparation method thereof, the steel plate have good welding performance.
Background technique
As engineering machinery develops to directions such as equipment enlargement, lightweight, heavy loads, high strength steel has shown new material
Ever-increasing trend, intensity rank is presented in bright prospects in the application of downstream process deeply industry chain, high-strength steel sheet dosage
Equal raisings are also quickly.In construction machinery product, welding structural element accounts for about the 50%~70% of main screw lift.Since structural member is wanted
Cyclic loading complicated and changeable is born, it is therefore desirable to which steel yield strength with higher and fatigue limit, good impact are tough
Property and cold formability and excellent welding performance.Constructional Machinery is selecting steel due to being mostly that plate welding forms
When plate, high-strength steel sheet is also required to have excellent welding performance.
Current steel for engineering machinery all joined Ni, Mo, such as Zhang Hong et al. (rainbow etc., quenching and tempering type high-strength steel Q690
The development of cut deal, heat processing technique, the 12nd phase of volume 39 in 2010) a kind of quenching and tempering type high-strength steel Q690 is described, it adopts
With low-carbon and the ingredient design scheme of Mo-Ni-B microalloying, increases manufacturing cost, do not refer to quenching and tempering type high-strength steel
The preheating temperature of Q690；Zhao Yan blueness et al. (organization and performance after Zhao Yanqing etc., 690MPa grades of low-carbon bainite steel temperings, gold
Belong to heat treatment, the 10th phase of volume 35 in October, 2010) a kind of 690MPa grades of low-carbon bainite steel is described, also use Ni, Mo etc.
Precious metal improves the mechanical property of steel plate, causes increased costs；Zhang Yun swallow et al. (Zhang Yun swallow etc., heat treatment process pair
690MPa grade high-strength structural rigidity can influence, steel research, the 5th phase of volume 35 in October, 2007) describe the change of Q690
Other alloys such as study point, the difference of mechanical property, burning optimization on line and heat-treated offline microscopic structure, and also use Mo
Member usually enhances the performance of steel plate, is not also illustrated to its preheating temperature.
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
The low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment, the chemical component and mass percent of the steel plate are as follows: C:0.09
~0.15%, Si:0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤0.010%, Nb:0.04~
0.08%, V:0.05~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤0.030%, Alt:0.020
~0.050%, N≤0.005%, O≤0.004%, remaining is iron and other inevitable impurity.
Preferably, the chemical component and mass percent of above-mentioned steel plate are as follows: C:0.12%, Si:0.375%, Mn:
1.665%, P:0.014%, S:0.007%, Nb:0.06%, V:0.065%, Ti:0.015%, Cr:0.40%, La:
0.020%, Alt:0.035%, N:0.0034%, O:0.0018%, remaining is iron and other inevitable impurity.
Preferably, when above-mentioned steel plate welds under the conditions of preheating temperature is less than 60 DEG C in oblique Y groove welding crack test,
The surface of steel plate cracking breakout and section crack rate are zero.
Preferably, the microscopic structure of above-mentioned steel plate is based on tempered sorbite.Tempered sorbite is that one kind of martensite is returned
Fire tissue, is the mixture of ferrite and granular carbide.Ferrite at this time has been substantially carbon-free degree of supersaturation, carbide
Also it is stable type carbide, therefore is a kind of statenchyma under tempered sorbite room temperature.It is with good toughness and plasticity, together
When intensity with higher, therefore there is good comprehensive mechanical property.
In another aspect of this invention, high-strength the present invention provides low preheating temperature 690MPa grades of above-mentioned rare earth treatment
The preparation method of steel plate, the method includes the steps: molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling, control are cold
But, align and be heat-treated, wherein molten iron pretreatment includes desulfurization, decarburization, dephosphorization treatment；It includes converter that the step, which is smelted,
Smelting, external refining, RH furnace vacuum outgas；Slab is obtained after the continuous casting step, the slab includes following mass percent
Chemical component: C:0.09~0.15%, Si:0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤
0.010%, Nb:0.04~0.08%, V:0.05~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤
0.030%, Alt:0.020~0.050%, N≤0.005%, O≤0.004%.
Preferably, slab heating temperature is 1200~1260 DEG C in above-mentioned slab heating stepses.
Preferably, above-mentioned controlled rolling step includes roughing and finish rolling, wherein the roughing start rolling temperature be 1100 DEG C~
1150 DEG C, finishing temperature is 980 DEG C~1050 DEG C, and single pass reduction ratio >=10% accumulates reduction ratio >=60%, to the roughing
2.5~3.5 times with a thickness of finished product thickness start the finish rolling, finish rolling start rolling temperature≤950 DEG C, single pass reduction ratio afterwards
>=12%, reduction ratio >=63% is accumulated, finishing temperature range is 800 DEG C~880 DEG C.
Preferably, above-mentioned control is cooling in straightening step, and the cooling cooling rate with 8~17 DEG C/s of control is cooling
It is aligned after to 580~640 DEG C using straightener.
Preferably, above-mentioned heat treatment step includes surface of steel plate ball blast, is then heated to 920~940 DEG C of heat preservation 15-
25min quenching, in 500~600 DEG C of heat preservation 8~12min temperings.
Based on above scheme, the present invention obtains a kind of addition rare earth but Ni, Mo is not added and with low preheating temperature
690MPa high-strength steel reduces costs and improves comprehensive mechanical property by rare earth treatment, extends service life, create good
Good economic benefit.And pass through oblique Y groove welding crack test: when being welded under the conditions of preheating temperature is less than 60 DEG C, the height
Strong steel surface cracking breakout and section crack rate are zero, illustrate that the 690MPa high-strength steel that the present invention obtains has lower preheating temperature
Degree, while keeping higher toughness and good welding performance.Meanwhile method provided by the invention uses Wide and Thick Slab slab for heat
Raw material is rolled, is heated, controlled rolling and controlled cooling, heat treatment (quenching+high tempering), is finally obtained with low-welding crack-sensitive
Steel plate, the microscopic structure of the steel plate are to have good comprehensive mechanical property based on tempered sorbite.
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 photomacrograph of according to embodiments of the present invention 1 welded specimen (under the conditions of 40 DEG C of preheating)；
Fig. 2 is the photomacrograph of according to embodiments of the present invention 1 welded specimen (under the conditions of 30 DEG C of preheating).
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.
For one or more problems existing in the prior art, it is an object of the present invention to provide a kind of rare earth treatment
The 690MPa grade high strength steel plate with low preheating temperature, another object is to provide the preparation method of the high strength steel plate.
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 the low preheating temperature 690MPa grades high of rare earth treatment
Strong steel plate, the chemical component and mass percent of the steel plate are as follows: C:0.09~0.15%, Si:0.30~0.45%, Mn:
1.58~1.75%, P≤0.02%, S≤0.010%, Nb:0.04~0.08%, V:0.05~0.08%, Ti:0.010~
0.020%, Cr:0.20~0.40%, La≤0.030%, Alt:0.020~0.050%, N≤0.005%, O≤0.004%,
Remaining is iron and other inevitable impurity.Such as the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment of the invention
Chemical component and mass percent can be with are as follows: C:0.09%, Si:0.45%, Mn:1.58%, P:0.02%, S:0.010%,
Nb:0.08%, V:0.05%, Ti:0.020%, Cr:0.20%, La:0.030%, Alt:0.020%, N:0.005%, O:
0.004%, remaining is iron and other inevitable impurity；Or C:0.15%, Si:0.30%, Mn:1.75%, P:0.01%,
S:0.008%, Nb:0.08%, V:0.05%, Ti:0.020%, Cr:0.20%, La:0.020%, Alt:0.050%, N:
0.005%, O:0.003%, remaining is iron and other inevitable impurity；Or C:0.12%, Si:0.40%, Mn:
1.65%, P:0.02%, S:0.010%, Nb:0.06%, V:0.06%, Ti:0.015%, Cr:0.30%, La:0.025%,
Alt:0.035%, N:0.005%, O:0.004%, remaining is iron and other inevitable impurity etc..
According to a preferred embodiment of the present invention, the chemical component and mass percent of above-mentioned steel plate are as follows: C:0.12%,
Si:0.375%, Mn:1.665%, P:0.014%, S:0.007%, Nb:0.06%, V:0.065%, Ti:0.015%, Cr:
0.40%, La:0.020%, Alt:0.035%, N:0.0034%, O:0.0018%, remaining is inevitable with other for iron
Impurity.
According to a preferred embodiment of the present invention, above-mentioned steel plate works as preheating temperature in oblique Y groove welding crack test
When welding under the conditions of less than 60 DEG C, the surface of steel plate cracking breakout and section crack rate are zero.
According to a preferred embodiment of the present invention, the microscopic structure of above-mentioned steel plate is based on tempered sorbite.It is tempered rope
Family name's body is a kind of tempered structure of martensite, is the mixture of ferrite and granular carbide.Ferrite at this time has been basic
Carbon-free degree of supersaturation, carbide are also stable type carbide, therefore are a kind of statenchyma under tempered sorbite room temperature.It has
There are good toughness and plasticity, while intensity with higher, therefore there is good comprehensive mechanical property.
In second embodiment of the present invention, the present invention provides the low preheating temperature 690MPa of above-mentioned rare earth treatment
The preparation method of grade high strength steel plate, the method includes the steps: molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling,
Control is cooling, aligns and is heat-treated, wherein molten iron pretreatment includes desulfurization, decarburization, dephosphorization treatment；The step smelts packet
Include converter smelting, external refining, RH furnace vacuum outgas；After continuous casting (the electromagnetic agitation, slighter compress) step, by clearing up, delaying
Slab is obtained after cold, quality examination, the slab includes the chemical component of following mass percent: C:0.09~0.15%, Si:
0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤0.010%, Nb:0.04~0.08%, V:0.05~
0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤0.030%, Alt:0.020~0.050%, N≤
0.005%, O≤0.004%.
According to a preferred embodiment of the present invention, slab heating temperature is 1200~1260 in above-mentioned slab heating stepses
℃。
According to a preferred embodiment of the present invention, above-mentioned controlled rolling step includes roughing and finish rolling, wherein described thick
Rolling start rolling temperature is 1100 DEG C~1150 DEG C, and finishing temperature is 980 DEG C~1050 DEG C, single pass reduction ratio >=10%, accumulation pressure
Lower rate >=60%, 2.5~3.5 times with a thickness of finished product thickness after the roughing start the finish rolling, the finish rolling open rolling temperature
≤ 950 DEG C of degree, single pass reduction ratio >=12% accumulate reduction ratio >=63%, and finishing temperature range is 800 DEG C~880 DEG C.
According to a preferred embodiment of the present invention, above-mentioned control is cooling and straightening step in, the control cools down with 8~
The cooling rate of 17 DEG C/s is aligned after being cooled to 580~640 DEG C using straightener.
According to a preferred embodiment of the present invention, above-mentioned heat treatment step includes surface of steel plate ball blast, is then heated to
920~940 DEG C of heat preservation 15-25min quenchings, in 500~600 DEG C of heat preservation 8~12min temperings.
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 the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment
Molten iron pretreatment is smelted, continuous casting: molten iron is subjected to desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization,
LF external refining and RH furnace vacuum outgas are carried out, then continuous casting (electromagnetic agitation, slighter compress) is carried out, by cleaning, slow cooling, matter
Amount obtains slab after checking.
The chemical component of gained slab is as shown in table 1 below:
1 Chemical Composition in Cast Billet of table and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | V | Ti | Cr | La | O | N |
| 0.09 | 0.30 | 1.58 | 0.010 | 0.005 | 0.020 | 0.040 | 0.050 | 0.010 | 0.20 | 0.010 | 0.0021 | 0.0032 |
Slab heating, controlled rolling, control is cooling, aligns: slab being heated to 1200 DEG C and is come out of the stove, high-pressure water descaling is laggard
Row rolling, 980 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=10%, accumulates reduction ratio by 1100 DEG C of roughing start rolling temperature
62%, to 2.5 times of beginning finish rolling with a thickness of finished product thickness, 930 DEG C of finish rolling start rolling temperature, the two-stage guarantees single pass reduction ratio
It is >=12%, accumulates reduction ratio 65%, finishing temperature is 800 DEG C, is cooled to 580 DEG C after finish rolling with the cooling rate of 8 DEG C/s, then send
It is aligned toward straightener.
Heat treatment: steel plate carries out shotblasting after surface quality inspection, and steel plate is then heated to 920 DEG C of guarantors
It quenches within temperature 20 minutes, the tempering of heat preservation 10 minutes is carried out at 500 DEG C.
Oblique Y groove welding crack test: it is welded under the conditions of 40 DEG C, 30 DEG C of preheating temperature, testing result is as shown in table 2 below.
And the photomacrograph of welded specimen, can obviously see under the conditions of Fig. 1 and Fig. 2 also respectively illustrate 40 DEG C and 30 DEG C of preheating temperature
It is zero to steel plate sample face crack rate and section crack rate, welding performance shows well.
The oblique Y groove welding crack test result of table 2
Embodiment 2: the preparation of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment
Molten iron pretreatment is smelted, continuous casting: molten iron is subjected to desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization,
LF external refining and RH furnace vacuum outgas are carried out, then continuous casting (electromagnetic agitation, slighter compress) is carried out, by cleaning, slow cooling, matter
Amount obtains slab after checking.
The chemical component of gained slab is as shown in table 3 below:
3 Chemical Composition in Cast Billet of table and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | V | Ti | Cr | La | O | N |
| 0.12 | 0.375 | 1.665 | 0.014 | 0.007 | 0.035 | 0.060 | 0.065 | 0.015 | 0.40 | 0.020 | 0.0018 | 0.0034 |
Slab heating, controlled rolling, control is cooling, aligns: slab being heated to 1230 DEG C and is come out of the stove, high-pressure water descaling is laggard
Row rolling, 1015 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=11%, accumulates reduction ratio by 1125 DEG C of roughing start rolling temperature
63%, start finish rolling when with a thickness of 3.0 times of finished product thickness, 930 DEG C of finish rolling start rolling temperature, guarantee single pass reduction ratio be >=
13%, reduction ratio 66% is accumulated, finishing temperature is 840 DEG C, is cooled to 610 DEG C after finish rolling with the cooling rate of 12.5 DEG C/s, then send
It is aligned toward straightener.
Heat treatment: steel plate carries out shotblasting after surface quality inspection, and steel plate is then heated to 930 DEG C of guarantors
It quenches within temperature 20 minutes, the tempering of heat preservation 10 minutes is carried out at 550 DEG C.
Oblique Y groove welding crack test: it is welded under the conditions of 20 DEG C, 10 DEG C of preheating temperature, testing result see the table below 4, by table 4
When welding under the conditions of 20 DEG C, 10 DEG C of preheating temperature known to middle data, steel plate sample face crack rate and section crack rate are zero,
Welding performance shows well.
The oblique Y groove welding crack test result of table 4
Embodiment 3: the preparation of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment
Molten iron pretreatment is smelted, continuous casting: molten iron is subjected to desulfurization pretreatment, using top and bottom combined blown converter decarburization, dephosphorization,
LF external refining and RH furnace vacuum outgas are carried out, then continuous casting (electromagnetic agitation, slighter compress) is carried out, by cleaning, slow cooling, matter
Amount obtains slab after checking.
The chemical component of gained slab is as shown in table 5 below:
5 Chemical Composition in Cast Billet of table and mass percent (%)
| C | Si | Mn | P | S | Alt | Nb | V | Ti | Cr | La | O | N |
| 0.15 | 0.45 | 1.75 | 0.015 | 0.010 | 0.050 | 0.080 | 0.080 | 0.02 | 0.20 | 0.015 | 0.0016 | 0.0030 |
Slab heating, controlled rolling, control is cooling, aligns: slab being heated to 1260 DEG C and is come out of the stove, high-pressure water descaling is laggard
Row rolling, 1050 DEG C of finishing temperature, guarantees that single pass reduction ratio is >=11%, accumulates reduction ratio by 1150 DEG C of roughing start rolling temperature
63%, start finish rolling when with a thickness of 3.5 times of finished product thickness, 930 DEG C of finish rolling start rolling temperature, guarantee single pass reduction ratio be >=
13%, reduction ratio 66% is accumulated, finishing temperature is 880 DEG C, is cooled to 640 DEG C after finish rolling with the cooling rate of 17 DEG C/s, is sent to
Straightener aligning.
Heat treatment: steel plate carries out shotblasting after surface quality inspection, and steel plate is then heated to 940 DEG C of guarantors
It quenches within temperature 20 minutes, the tempering of heat preservation 10 minutes is carried out at 600 DEG C.
Oblique Y groove welding crack test: it is welded under the conditions of 15 DEG C, 5 DEG C of preheating temperature, testing result see the table below 6, by table 6
When welding under the conditions of 15 DEG C, 5 DEG C of preheating temperature known to middle data, steel plate sample face crack rate and section crack rate are zero,
Welding performance shows well.
The oblique Y groove welding crack test result of table 6
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 (9)
1. a kind of low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment, which is characterized in that the chemical component of the steel plate
And mass percent are as follows: C:0.09~0.15%, Si:0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤
0.010%, Nb:0.04~0.08%, V:0.05~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤
0.030%, Alt:0.020~0.050%, N≤0.005%, O≤0.004%, remaining is inevitably miscellaneous with other for iron
Matter.
2. the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment described in claim 1, which is characterized in that the steel plate
Chemical component and mass percent are as follows: C:0.12%, Si:0.375%, Mn:1.665%, P:0.014%, S:0.007%,
Nb:0.06%, V:0.065%, Ti:0.015%, Cr:0.40%, La:0.020%, Alt:0.035%, N:0.0034%, O:
0.0018%, remaining is iron and other inevitable impurity.
3. the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment of any of claims 1 or 2, which is characterized in that described
When steel plate welds under the conditions of preheating temperature is less than 60 DEG C in oblique Y groove welding crack test, the surface of steel plate cracking breakout
It is zero with section crack rate.
4. the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment of any of claims 1 or 2, which is characterized in that described
The microscopic structure of steel plate is based on tempered sorbite.
5. the preparation side of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment of any of claims 1-4
Method, which is characterized in that the method includes the steps: molten iron pretreatment, smelting, continuous casting, slab heating, controlled rolling, control are cold
But, align and be heat-treated, wherein molten iron pretreatment includes desulfurization, decarburization, dephosphorization treatment；It includes converter that the step, which is smelted,
Smelting, external refining, RH furnace vacuum outgas；Slab is obtained after the continuous casting step, the slab includes following mass percent
Chemical component: C:0.09~0.15%, Si:0.30~0.45%, Mn:1.58~1.75%, P≤0.02%, S≤
0.010%, Nb:0.04~0.08%, V:0.05~0.08%, Ti:0.010~0.020%, Cr:0.20~0.40%, La≤
0.030%, Alt:0.020~0.050%, N≤0.005%, O≤0.004%.
6. the preparation method of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment described in claim 5, feature exist
In slab heating temperature is 1200~1260 DEG C in the slab heating stepses.
7. the preparation method of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment described in claim 5, feature exist
In, the controlled rolling step includes roughing and finish rolling, wherein the roughing start rolling temperature is 1100 DEG C~1150 DEG C, finish to gauge temperature
Degree is 980 DEG C~1050 DEG C, and single pass reduction ratio >=10% accumulates reduction ratio >=60%, with a thickness of finished product after the roughing
2.5~3.5 times of thickness start the finish rolling, finish rolling start rolling temperature≤950 DEG C, single pass reduction ratio >=12%, accumulation
Reduction ratio >=63%, finishing temperature range are 800 DEG C~880 DEG C.
8. the preparation method of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment described in claim 5, feature exist
In the control is cooling in straightening step, and the control cooling is cooled to 580~640 DEG C with the cooling rate of 8~17 DEG C/s
It is aligned afterwards using straightener.
9. the preparation method of the low preheating temperature 690MPa grades of high strength steel plates of rare earth treatment described in claim 5, feature exist
In the heat treatment step includes surface of steel plate ball blast, 920~940 DEG C of heat preservation 15-25min quenchings is then heated to, 500
~600 DEG C of heat preservation 8~12min temperings.
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| CN115491475A (en) * | 2022-10-12 | 2022-12-20 | 包头钢铁（集团）有限责任公司 | Preparation method of rare earth microalloyed low-cost high-hardness plastic die steel P20 |
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