CN105861926A - Dual phase steel with tensile strength of 1000 MPa and production method thereof - Google Patents
Dual phase steel with tensile strength of 1000 MPa and production method thereof 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- 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
- C21D8/0236—Cold rolling
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
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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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- 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 invention discloses a dual phase steel with tensile strength of 1000 MPa and a production method thereof. The dual phase steel is composed of the following chemical components in percentage by weight: 0.08%-0.11% of C, 0.2%-0.6% of Si, 2.0%-2.5% of Mn, at most 0.01% of P, at most 0.01% of S, 0.02%-0.06% of Al, 0.4%-0.6% of Cr, 0.02%-0.05% of Ti, at most 0.003% of N, and the balance of Fe and inevitable impurities. The method solves the technical problem of how to lower the alloy cost and enhance the reaming property and delayed fracture resistance of the material on the premise of satisfying the strength requirement.
Description
Technical field
The present invention relates to Steel material technical field, particularly to the two-phase of a kind of tensile strength 1000MPa
Steel and production method thereof.
Background technology
The lightweight of automobile, it is simply that on the premise of the intensity ensureing automobile and security performance, as far as possible
Ground reduces the kerb weight of automobile, thus improves the dynamic property of automobile, reduces fuel consumption, reduces row
Gas pollutes.Automotive light weight technology the most not only becomes the task of top priority of Domestic Automotive Industry development, also becomes generation
The trend of boundary's development of automobile.Dual phase steel is due to good comprehensive mechanical property, with traditional general steel plate
Compare the unrivaled advantage having so that dual phase steel starts to be answered at automotive safety member arts
With.
Along with the increase of automobile component requirement of strength, the requirement to material molding also accordingly increases.Punching
Molded material requirements material has low yield tensile ratio, but the materials such as flange bending, reaming and roll-in become
Type then requires that material has higher yield tensile ratio.In dual phase steel alloy system select, soft or hard phase morphology and
Distribution all will directly affect mechanical property and the final molding performance thereof of dual phase steel.
It addition, dual phase steel is made up of the martensite island of Dispersed precipitate on ferrite matrix and matrix, 1000MPa
In rank dual phase steel, martensite island volume fraction is up to about 20-30%.Owing to martensite has higher hydrogen
Crisp sensitivity, its under arms during will there is the risk of delayed fracture.In auto parts, dual phase steel is multiplex
In body structural members such as crossbeam longerons, once there is delayed fracture problem, be fatal to vehicle safety.
Summary of the invention
The present invention provides dual phase steel and the production method thereof of a kind of tensile strength 1000MPa, solve as
Reduce cost of alloy on the basis of where meeting requirement of strength, improve the reaming performance of material and resistance to delay
The technical problem of fracture property, has reached to improve the reaming performance of dual phase steel and resistance for delayed fracture
Technique effect.
For solving above-mentioned technical problem, the invention provides the dual phase steel of a kind of tensile strength 1000MPa,
The chemical composition of described dual phase steel is by weight percentage: C:0.08%～0.11%；Si:0.2%-0.6%；
Mn:2.0%～2.5%；P :≤0.01%；S :≤0.01%；Al:0.02%～0.06%；Cr:
0.4%-0.6%；Ti:0.02%-0.05%；N :≤0.003%, remaining is Fe and the most miscellaneous
Matter.
Preferably, described Ti element and described C element combine and form TiC nanometer precipitated phase.
Preferably, the tensile strength of described dual phase steel is 1000MPa, and yield tensile ratio is more than 0.65.
Preferably, in described dual phase steel, notched tensile strength rate of descent RNS is less than 10%.
Preferably, the metallographic structure of described dual phase steel includes Lycoperdon polymorphum Vitt ferrite, brilliant white martensite and lacks
Amount black bainite.
The application also provides for the production method of the dual phase steel of a kind of tensile strength 1000MPa, is used for producing
Above-mentioned dual phase steel, described production method includes:
To smelting molten steel and cast continuous casting billet；
To described continuous casting billet hot rolling, it is thus achieved that hot rolled plate；
Described hot rolled plate is carried out cold rolling, it is thus achieved that chill strip steel；
Described chill strip steel is carried out continuous annealing, obtains described dual phase steel.
Preferably, described smelting also casts continuous casting billet, particularly as follows: by molten steel through converter smelting, and adopt
With continuous casting mode cast steel.
Preferably, the heating-up temperature of described hot rolling is 1210 DEG C～1300 DEG C, the finish to gauge temperature of described hot rolling
Degree is 850 DEG C～890 DEG C, and the coiling temperature of described hot rolling is 620 DEG C～680 DEG C.
Preferably, the preheating temperature of described continuous annealing is 230 DEG C～270 DEG C, and heating-up temperature is
780 DEG C～810 DEG C, soaking temperature is 780 DEG C～810 DEG C, and slow cooling outlet temperature is 680 DEG C～710 DEG C,
Rapid cooling outlet temperature is 230 DEG C～270 DEG C, and overaging temperature is 230 DEG C～270 DEG C, finishing elongation percentage
It is 0.3%～0.5%.
Preferably, the heating-up temperature of described continuous annealing is specially 790 DEG C～800 DEG C, described moves back continuously
The soaking temperature of fire is specially 790 DEG C～800 DEG C.
The application has the beneficial effect that:
The dual phase steel of a kind of tensile strength 1000MPa that the application provides and production method thereof, do not adding
On the basis of adding alloy relatively costly elements Mo element and Nb element, it is thus achieved that higher reaming performance
And the dual phase steel of resistance for delayed fracture, utilize Ti element and C element to combine and generate the analysis of TiC nanometer
Go out and make crystal grain refine mutually, simultaneously Dispersed precipitate nanometer in the ferrite base body of described two-phase steel grade
Precipitated phase provides enough precipitation intensity, so that the yield strength of material improves, yield tensile ratio is big
In 0.65, reduce the nonhomogeneous hardness that soft or hard is biphase, and then improve the reaming performance of material.And it is big
The TiC particle of amount fixes the diffusible hydrogen content of described dual phase steel as irreversible hydrogen trap, prevents
Hydrogen embrittlement, it is provided that the resistance for delayed fracture of described dual phase steel, solves and how to meet requirement of strength
On the basis of reduce cost of alloy, the technology improving the reaming performance of material and resistance for delayed fracture is asked
Topic.
Accompanying drawing explanation
In order to be illustrated more clearly that the embodiment of the present invention or technical scheme of the prior art, below will be to reality
Execute the required accompanying drawing used during example describes to be briefly described, it should be apparent that, attached in describing below
Figure is only some embodiments of the present invention.
Fig. 1 is the metallographic group of the dual phase steel of a kind of tensile strength 1000MPa of the application better embodiment
Knit figure；
Fig. 2 is that the stretching at a slow speed before and after the dual phase steel sample of tensile strength 1000MPa in Fig. 1 is flushed with hydrogen is bent
Line；
Fig. 3 is stretching fracture at a slow speed after the dual phase steel sample of tensile strength 1000MPa in Fig. 1 is flushed with hydrogen
Shape appearance figure；
Fig. 4 is the metallographic of the dual phase steel sample TiC nanometer precipitated phase of tensile strength 1000MPa in Fig. 1
Organization charts；
Fig. 5 is the life of the dual phase steel of the application a kind of tensile strength 1000MPa of another better embodiment
The flow chart of product method.
Detailed description of the invention
The embodiment of the present application is by providing dual phase steel and the producer thereof of a kind of tensile strength 1000MPa
Method, solves and how to reduce cost of alloy on the basis of meeting requirement of strength, improve the reaming of material
Performance and the technical problem of resistance for delayed fracture, reached improve the reaming performance of dual phase steel and resistance to prolong
The technique effect of fracture property late.
Technical scheme in the embodiment of the present application is for solving above-mentioned technical problem, and general thought is as follows:
A kind of dual phase steel of tensile strength 1000MPa, the chemical composition of described dual phase steel percentage by weight
Than being:
C:0.08%～0.11%；Si:0.2%-0.6%；Mn:2.0%～2.5%；P :≤0.01%；
S :≤0.01%；Al:0.02%～0.06%；Cr:0.4%-0.6%；Ti:0.02%-0.05%；N:
≤ 0.003%, remaining is Fe and inevitable impurity.
The application, on the basis of without cost of alloy higher elements Mo element and Nb element, obtains
Reaming performance that must be higher and the dual phase steel of resistance for delayed fracture, utilize Ti element and C element knot
Symphysis becomes TiC nanometer precipitated phase to make crystal grain refine, and Dispersed precipitate is in the ferrum of described two-phase steel grade simultaneously
Nanometer precipitated phase in ferritic matrix provides enough precipitation intensity, so that the tension of material is strong
Degree reaches 1000MPa, and yield tensile ratio is more than 0.65, reduces the nonhomogeneous hardness that soft or hard is biphase, Jin Ergai
It is apt to the reaming performance of material.And substantial amounts of TiC particle is fixed described as irreversible hydrogen trap
The diffusible hydrogen content of dual phase steel, prevents hydrogen embrittlement, it is provided that the resistance for delayed fracture of described dual phase steel,
Solve and how on the basis of meeting requirement of strength, to reduce cost of alloy, improve the reaming performance of material
And the technical problem of resistance for delayed fracture.
In order to be better understood from technique scheme, below in conjunction with Figure of description and concrete reality
Technique scheme is described in detail by mode of executing.
Embodiment one
In order to solve reaming performance and the delayed fracture resistance of steel strength requirement and material in prior art
The technical problem that can simultaneously meet, the application provides the dual phase steel of a kind of tensile strength 1000MPa.
The chemical composition of described dual phase steel is by weight percentage:
C:0.08%～0.11%；Si:0.2%-0.6%；Mn:2.0%～2.5%；P :≤0.01%；
S :≤0.01%；Al:0.02%～0.06%；Cr:0.4%-0.6%；Ti:0.02%-0.05%；N:
≤ 0.003%, remaining is Fe and inevitable impurity.
The metallographic structure figure of the dual phase steel of described tensile strength 1000MPa and tensile strength 1000MPa
The metallographic structure figure of dual phase steel sample TiC nanometer precipitated phase, as shown in Figure 1 and Figure 4.
Above-mentioned main alloy element effect and the scope of restriction are as follows:
Carbon C: carbon is most important solution strengthening element in dual phase steel, stable Austria in annealing process
Family name's body, thus in cooling procedure, obtain enough martensite volumes to ensure the intensity of dual phase steel.But,
The increase of carbon content also significantly improves the delayed fracture sensitivity of steel, and therefore carbon content needs to do the upper limit
Clearly limiting, the carbon element content that the present invention uses is 0.08%～0.11%.
Silicon Si: element silicon contributes to expanding two-phase section, is dissolved in ferrite and plays strengthening effect, moreover it is possible to
Reduce Hydrogen diffusion coefficient, thus reduce the spreading rate of hydrogen induced cracking.But silicone content increases easily
Causing hot rolling surface red phosphorus defect to increase, it is unfavorable that Surface Quality controls, and therefore silicone content needs upper
Limit is done and is clearly limited, and the silicon content that the present invention uses is 0.2%～0.6%.
Manganese Mn: manganese element is also the important element of solution strengthening, stable austenite, strong to dual phase steel
Change and there is important function.But Mn easily combines generate MnS field trash with S, hydrogen induced cracking is often
Germinate at the MnS place of being mingled with and cause delayed fracture.The present invention use manganese element content be 2.0%～
2.5%.
Phosphorus P: P elements, as harmful element, will dramatically increase delayed fracture sensitivity at Grain Boundary Segregation,
The phosphorus element content that the present invention uses controls less than or equal to 0.01%.
Sulfur S: element sulphur is as harmful element, and element sulphur mainly prevents from being combined generation MnS with Mn element
Increasing delayed fracture sensitivity, the sulfur content that the present invention uses controls less than or equal to 0.01%.
Aluminum Al: aluminium element is as making steel main deoxidant element, to two-phase section effect and Si element phase
Seemingly, the aluminium element content that the present invention uses is 0.02%～0.06%.
Chromium Cr: chromium element dramatically increases the quenching degree of steel, before without relatively costly Mo element
Putting, Cr element has important effect for the formation of martensite.It addition, Cr can suppress along brilliant
The generation of fracture, thus improve the delayed fracture drag of steel.The chromium constituent content that the present invention uses is
0.4%～0.6%.
Titanium Ti: titanium elements is carbide, and titanium elements is combined generation nanometer with carbon
Grain TiC, can play the effect of crystal grain thinning and precipitation strength.TiC has higher trap simultaneously
Can, resistance for delayed fracture can be significantly improved as irreversible trap.The titanium elements that the present invention uses
Content is 0.02%～0.05%.
Nitrogen N: nitrogen element interaction is similar to C, but in order to avoid N with Ti is combined generation large scale TiN
Deteriorating performance, the nitrogen element content that the present invention uses controls less than or equal to 0.003%.
Preferably, main alloy element effect and the scope of restriction that the application provides are as follows, refer to table
1:
Table 1 dual phase steel chemical composition (wt%)
| Embodiment | C | Si | Mn | P | S | Al | Cr | Ti | N |
| 1 | 0.095 | 0.35 | 2.3 | 0.007 | 0.005 | 0.035 | 0.55 | 0.027 | 0.0027 |
| 2 | 0.091 | 0.36 | 2.4 | 0.008 | 0.005 | 0.033 | 0.54 | 0.026 | 0.0029 |
| 3 | 0.099 | 0.35 | 2.3 | 0.007 | 0.004 | 0.039 | 0.51 | 0.030 | 0.003 |
| 4 | 0.089 | 0.25 | 2.1 | 0.006 | 0.003 | 0.023 | 0.44 | 0.036 | 0.0015 |
| 5 | 0.087 | 0.40 | 2.2 | 0.005 | 0.007 | 0.045 | 0.47 | 0.046 | 0.0019 |
| 6 | 0.084 | 0.45 | 2.45 | 0.004 | 0.008 | 0.055 | 0.58 | 0.041 | 0.0009 |
| 7 | 0.10 | 0.50 | 2.35 | 0.003 | 0.006 | 0.40 | 0.48 | 0.048 | 0.0012 |
The mechanical property of described dual phase steel specifically includes, and refers to table 2 Mechanical Properties of Dual Phase Steels table.
Table 2 Mechanical Properties of Dual Phase Steels table
The tensile strength that the application provides is more than 1000MPa, the yield tensile ratio dual phase steel more than 0.65,
On the basis of cost of alloy higher elements Mo element and Nb element, it is thus achieved that higher reaming
Performance and the dual phase steel of resistance for delayed fracture, utilize Ti element and C element to combine generation TiC and receive
Rice precipitated phase makes crystal grain refine, and Dispersed precipitate is in the ferrite base body of described two-phase steel grade simultaneously
Nanometer precipitated phase provides enough precipitation intensity, so that the tensile strength of material reaches
1000MPa, yield tensile ratio is more than 0.65, reduces the nonhomogeneous hardness that soft or hard is biphase, and then improve material
The reaming performance of material.And substantial amounts of TiC particle fixes described dual phase steel as irreversible hydrogen trap
Diffusible hydrogen content, prevent hydrogen embrittlement, it is provided that the resistance for delayed fracture of described dual phase steel, solve
How on the basis of meeting the requirement of strength of 1000MPa, to reduce cost of alloy, improve the reaming of material
Performance and the technical problem of resistance for delayed fracture.
Embodiment two
Based on same inventive concept, the application also provides for the dual phase steel of a kind of tensile strength 1000MPa
Production method, the dual phase steel of described tensile strength 1000MPa in production example one.As
Shown in Fig. 5, the production method of the dual phase steel of described tensile strength 1000MPa, refer to Fig. 5,
Described production method comprises the following steps:
Step 110, to smelting molten steel and cast continuous casting billet.
Specifically, described to smelting molten steel and cast continuous casting billet, it is specially molten steel through converter smelting,
And use continuous casting mode cast steel.Described molten steel is the molten steel of the dual phase steel of above-mentioned tensile strength 1000MPa.
Step 120, to described continuous casting billet hot rolling, it is thus achieved that hot rolled plate.
Specifically, the heating-up temperature of described hot rolling is 1210 DEG C～1300 DEG C, the finish to gauge temperature of described hot rolling
Degree is 850 DEG C～890 DEG C, and the coiling temperature of described hot rolling is 620 DEG C～680 DEG C.Table 3 is dual phase steel
Hot rolling technology embodiment.
Table 3 dual phase steel hot rolling technology embodiment
| Embodiment | Heating-up temperature | Finishing temperature | Coiling temperature | Hot rolled thickness | Cold-rolling thickness |
| 1 | 1250℃ | 873℃ | 669℃ | 4mm | 1.5mm |
| 2 | 1260℃ | 881℃ | 671℃ | 4mm | 1.5mm |
| 3 | 1255℃ | 877℃ | 663℃ | 4mm | 1.5mm |
Step 130, carries out cold rolling to described hot rolled plate, it is thus achieved that chill strip steel.
Step 140, carries out continuous annealing to described chill strip steel, obtains described dual phase steel.
Specifically, the preheating temperature of described continuous annealing process is 230 DEG C～270 DEG C, and heating-up temperature is
780 DEG C～810 DEG C, soaking temperature is 780 DEG C～810 DEG C, and slow cooling outlet temperature is 680 DEG C～710 DEG C,
Rapid cooling outlet temperature is 230 DEG C～270 DEG C, and overaging temperature is 230 DEG C～270 DEG C, finishing elongation percentage
Being 0.3%～0.5%, straightening elongation percentage is 0.
Preferably, the heating-up temperature of described continuous annealing is specially 790 DEG C～800 DEG C, described moves back continuously
The soaking temperature of fire is specially 790 DEG C～800 DEG C.Wherein, table 4 is dual phase steel continuous annealing process
Embodiment.
The embodiment of table 4 dual phase steel continuous annealing process
Through dual phase steel prepared by above-mentioned production technology, tensile strength is more than 1000MPa, and yield tensile ratio is big
In 0.65, refer to table 5.
The intensity embodiment of the dual phase steel after table 5 process
| Embodiment | Rm/MPa | Rp0.2/MPa | A80/% | Yield tensile ratio |
| 1 | 1008 | 680 | 11.5 | 0.675 |
| 2 | 1003 | 667 | 12.5 | 0.665 |
| 3 | 1016 | 706 | 11.0 | 0.695 |
Example one
Using 220 tons of converter smeltings in example one, the hot rolling target thickness of steel plate finished product is 4mm, cold rolling
Thickness is 1.5mm, concretely comprising the following steps of smelting:
S1: to smelting molten steel and cast continuous casting billet；Smelting process strictly controls P, S content, it is ensured that
Slab quality.The chemical composition of strand is as follows: calculate C:0.095wt% by percentage to the quality；Si:
0.35wt%；Mn:2.3wt%；P:0.007wt%；S:0.005wt%；Al:0.0035wt%；
Cr:0.55wt%；Ti:0.027wt%；N:0.0027wt%, remaining is Fe and inevitably
Impurity.
S2: to described continuous casting billet hot rolling, it is thus achieved that hot rolled plate；The heating-up temperature of described hot rolling is 1250 DEG C,
The finishing temperature of described hot rolling is 873 DEG C, and the coiling temperature of described hot rolling is 669 DEG C.Steel after hot rolling
Plate thickness is 4mm.
S3: described hot rolled plate is carried out cold rolling, it is thus achieved that chill strip steel；Described cold rolling after steel plate thickness be
1.5mm。
S4: described chill strip steel is carried out continuous annealing, obtains described dual phase steel.Described continuous annealing
The preheating temperature of technique is 250 DEG C, and heating-up temperature is 800 DEG C, and soaking temperature is 800 DEG C, and slow cooling goes out
Mouth temperature is 700 DEG C, and rapid cooling outlet temperature is 250 DEG C, and overaging temperature is 250 DEG C, and finishing extends
Rate is 0.4%, and straightening elongation percentage is 0.
The mechanical property of the dual phase steel finally given through above-mentioned steps be Rm be 1008MPa, Rp0.2
Being 11.5% for 680MPa, A80, yield tensile ratio is 0.675.
The steel obtaining above-mentioned steps in example one carries out reaming experiment, initial aperture 10mm, opens for the first time
Splitting back aperture is 15.19mm, and second time cracking back aperture is 15.08mm, third time cracking back aperture
For 15.22mm, calculating average pore size after ftractureing is 15.16mm, and hole expansibility is 51.6%.
The steel obtaining above-mentioned steps in example one utilizes electrochemical cathode hydrogen filling method, at 0.1mol/L
NaOH electrolyte uses difference be flushed with hydrogen system sample is flushed with hydrogen, stretch the most at a slow speed reality
Test, refer to the stress strain curve at a slow speed before and after the sample described in Fig. 2 is flushed with hydrogen.Utilize notched tensile strength
Rate of descent RNS (RNS=(1-σNB/σNB0) × 100%) evaluate its Hydrogen Embrittlement, σ NB,
σ NB0 is respectively flushed with hydrogen before and after's peak stress.Described dual phase steel RNS under the conditions of difference is flushed with hydrogen divides
It is not 3.1% (to be flushed with hydrogen condition 8mA/cm2× 72h) and 5.4% (it is flushed with hydrogen condition 16mA/cm2×72h)。
Refer to Fig. 3, Fig. 3 for stretching fracture pattern slow after being flushed with hydrogen.Fracture apperance is dimpled fracture, fracture
Mode is ductile rupture, illustrates that delayed fracture is insensitive.Referring to Fig. 4, Fig. 4 is sample ferrite
The TiC nanometer precipitated phase of Dispersed precipitate in matrix, serves precipitation strength effect and becomes the most not
Reversible hydrogen trap.
Example two
Using 220 tons of converter smeltings in example two, the hot rolling target thickness of steel plate finished product is 4mm, cold rolling
Thickness is 1.5mm, concretely comprising the following steps of smelting:
S1: to smelting molten steel and cast continuous casting billet；Smelting process strictly controls P, S content, it is ensured that
Slab quality.The chemical composition of strand is as follows: calculate C:0.091wt% by percentage to the quality；Si:
0.36wt%；Mn:2.4wt%；P:0.008wt%；S:0.005wt%；Al:0.0033wt%；
Cr:0.54wt%；Ti:0.026wt%；N:0.0029wt%, remaining is Fe and inevitably
Impurity.
S2: to described continuous casting billet hot rolling, it is thus achieved that hot rolled plate；The heating-up temperature of described hot rolling is 1260 DEG C,
The finishing temperature of described hot rolling is 881 DEG C, and the coiling temperature of described hot rolling is 671 DEG C.Steel after hot rolling
Plate thickness is 4mm.
S3: described hot rolled plate is carried out cold rolling, it is thus achieved that chill strip steel；Described cold rolling after steel plate thickness be
1.5mm。
S4: described chill strip steel is carried out continuous annealing, obtains described dual phase steel.Described continuous annealing
The preheating temperature of technique is 250 DEG C, and heating-up temperature is 795 DEG C, and soaking temperature is 795 DEG C, and slow cooling goes out
Mouth temperature is 695 DEG C, and rapid cooling outlet temperature is 250 DEG C, and overaging temperature is 250 DEG C, and finishing extends
Rate is 0.4%, and straightening elongation percentage is 0.
The mechanical property of the dual phase steel finally given through above-mentioned steps be Rm be 1003MPa, Rp0.2
Being 12.5% for 667MPa, A80, yield tensile ratio is 0.665.
The steel obtaining above-mentioned steps in example two carries out reaming experiment, initial aperture 10mm, opens for the first time
Splitting back aperture is 14.81mm, and second time cracking back aperture is 15.13mm, third time cracking back aperture
For 14.72mm, calculating average pore size after ftractureing is 14.89mm, and hole expansibility is 48.9%.
The steel obtaining above-mentioned steps in example two utilizes electrochemical cathode hydrogen filling method, at 0.1mol/L
NaOH electrolyte uses difference be flushed with hydrogen system sample is flushed with hydrogen, stretch the most at a slow speed reality
Test, evaluate its Hydrogen Embrittlement also with notched tensile strength rate of descent RNS.Described two-phase
Steel RNS under the conditions of difference is flushed with hydrogen is respectively 3.4% and (is flushed with hydrogen condition 8mA/cm2× 72h) and
5.7% (is flushed with hydrogen condition 16mA/cm2×72h).Fracture apperance is dimpled fracture, and fracture mode is toughness
Fracture, illustrates that delayed fracture is insensitive.The TiC nanometer analysis of Dispersed precipitate in sample ferrite matrix
Go out phase, serve precipitation strength effect and become a large amount of irreversible hydrogen trap.
Example three
Using 220 tons of converter smeltings in example three, the hot rolling target thickness of steel plate finished product is 4mm, cold rolling
Thickness is 1.5mm, concretely comprising the following steps of smelting:
S1: to smelting molten steel and cast continuous casting billet；Smelting process strictly controls P, S content, it is ensured that
Slab quality.The chemical composition of strand is as follows: calculate C:0.099wt% by percentage to the quality；Si:
0.35wt%；Mn:2.3wt%；P:0.007wt%；S:0.004wt%；Al:0.0039wt%；
Cr:0.51wt%；Ti:0.030wt%；N:0.003wt%, remaining is Fe and the most miscellaneous
Matter.
S2: to described continuous casting billet hot rolling, it is thus achieved that hot rolled plate；The heating-up temperature of described hot rolling is 1255 DEG C,
The finishing temperature of described hot rolling is 877 DEG C, and the coiling temperature of described hot rolling is 663 DEG C.Steel after hot rolling
Plate thickness is 4mm.
S3: described hot rolled plate is carried out cold rolling, it is thus achieved that chill strip steel；Described cold rolling after steel plate thickness be
1.5mm。
S4: described chill strip steel is carried out continuous annealing, obtains described dual phase steel.Described continuous annealing
The preheating temperature of technique is 250 DEG C, and heating-up temperature is 790 DEG C, and soaking temperature is 790 DEG C, and slow cooling goes out
Mouth temperature is 690 DEG C, and rapid cooling outlet temperature is 250 DEG C, and overaging temperature is 250 DEG C, and finishing extends
Rate is 0.4%, and straightening elongation percentage is 0.
The mechanical property of the dual phase steel finally given through above-mentioned steps be Rm be 1016MPa, Rp0.2
Being 11.0% for 706MPa, A80, yield tensile ratio is 0.695.
The steel obtaining above-mentioned steps in example three carries out reaming experiment, initial aperture 10mm, opens for the first time
Splitting back aperture is 16.69mm, and second time cracking back aperture is 16.45mm, third time cracking back aperture
For 16.10mm, calculating average pore size after ftractureing is 16.41mm, and hole expansibility is 64.1%.
The steel obtaining above-mentioned steps in example three utilizes electrochemical cathode hydrogen filling method, at 0.1mol/L
NaOH electrolyte uses difference be flushed with hydrogen system sample is flushed with hydrogen, stretch the most at a slow speed reality
Test, evaluate its Hydrogen Embrittlement also with notched tensile strength rate of descent RNS.Described two-phase
Steel RNS under the conditions of difference is flushed with hydrogen is respectively 2.9% and (is flushed with hydrogen condition 8mA/cm2× 72h) and 5.0% (fill
Hydrogen condition 16mA/cm2×72h).Fracture apperance is dimpled fracture, and fracture mode is ductile rupture, says
Bright delayed fracture is insensitive.The TiC nanometer precipitated phase of Dispersed precipitate in sample ferrite matrix, rises
Arrive precipitation strength effect and become a large amount of irreversible hydrogen trap.
The application has the beneficial effect that:
The dual phase steel of a kind of tensile strength 1000MPa that the application provides and production method thereof, do not adding
On the basis of adding alloy relatively costly elements Mo element and Nb element, it is thus achieved that higher reaming performance
And the dual phase steel of resistance for delayed fracture, utilize Ti element and C element to combine and generate the analysis of TiC nanometer
Go out and make crystal grain refine mutually, simultaneously Dispersed precipitate nanometer in the ferrite base body of described two-phase steel grade
Precipitated phase provides enough precipitation intensity, so that the tensile strength of material reaches 1000MPa,
Yield tensile ratio is more than 0.65, reduces the nonhomogeneous hardness that soft or hard is biphase, and then improves the hole expandability of material
Energy.And the diffusible hydrogen that substantial amounts of TiC particle fixes described dual phase steel as irreversible hydrogen trap contains
Amount, prevents hydrogen embrittlement, it is provided that the resistance for delayed fracture of described dual phase steel, solves and how to meet
Reduce cost of alloy on the basis of requirement of strength, improve reaming performance and the resistance for delayed fracture of material
Technical problem.
It should be noted last that, above detailed description of the invention is only in order to illustrate technical scheme
And unrestricted, although the present invention being described in detail with reference to example, the ordinary skill people of this area
Member should be appreciated that and can modify technical scheme or equivalent, without deviating from
The spirit and scope of technical solution of the present invention, it all should be contained ought in scope of the presently claimed invention
In.
Claims (10)
1. the dual phase steel of tensile strength 1000MPa, it is characterised in that the chemistry of described dual phase steel
Composition is by weight percentage:
C:0.08%～0.11%；Si:0.2%-0.6%；Mn:2.0%～2.5%；P :≤0.01%；
S :≤0.01%；Al:0.02%～0.06%；Cr:0.4%-0.6%；Ti:0.02%-0.05%；N:
≤ 0.003%, remaining is Fe and inevitable impurity.
2. dual phase steel as claimed in claim 1, it is characterised in that described Ti element and described C
Element combines and forms TiC nanometer precipitated phase.
3. dual phase steel as claimed in claim 1, it is characterised in that the tensile strength of described dual phase steel
For 1000MPa, yield tensile ratio is more than 0.65.
4. dual phase steel as claimed in claim 1, it is characterised in that breach tension in described dual phase steel
Intensity rate of descent RNS is less than 10%.
5. dual phase steel as claimed in claim 1, it is characterised in that the metallographic structure of described dual phase steel
Including Lycoperdon polymorphum Vitt ferrite, brilliant white martensite and a small amount of black bainite.
6. a production method for the dual phase steel of tensile strength 1000MPa, for producing such as claim
1 to 5 arbitrary described dual phase steel, it is characterised in that described production method includes:
To smelting molten steel and cast continuous casting billet；
To described continuous casting billet hot rolling, it is thus achieved that hot rolled plate；
Described hot rolled plate is carried out cold rolling, it is thus achieved that chill strip steel；
Described chill strip steel is carried out continuous annealing, obtains described dual phase steel.
7. production method as claimed in claim 6, it is characterised in that described smelting also casts continuous casting
Base, particularly as follows:
By molten steel through converter smelting, and use continuous casting mode cast steel.
8. production method as claimed in claim 6, it is characterised in that the heating-up temperature of described hot rolling
Being 1210 DEG C～1300 DEG C, the finishing temperature of described hot rolling is 850 DEG C～890 DEG C, the volume of described hot rolling
Qu Wendu is 620 DEG C～680 DEG C.
9. production method as claimed in claim 6, it is characterised in that the preheating of described continuous annealing
Temperature is 230 DEG C～270 DEG C, and heating-up temperature is 780 DEG C～810 DEG C, soaking temperature be 780 DEG C～
810 DEG C, slow cooling outlet temperature is 680 DEG C～710 DEG C, and rapid cooling outlet temperature is 230 DEG C～270 DEG C,
Overaging temperature is 230 DEG C～270 DEG C, and finishing elongation percentage is 0.3%～0.5%.
10. production method as claimed in claim 9, it is characterised in that adding of described continuous annealing
Hot temperature is specially 790 DEG C～800 DEG C, the soaking temperature of described continuous annealing be specially 790 DEG C～
800℃。
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| CN107460404A (en) * | 2017-07-17 | 2017-12-12 | 河钢股份有限公司 | A kind of yield strength 800MPa ultra-high strength strip steels and preparation method thereof |
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| CN108950405B (en) * | 2018-08-14 | 2020-02-18 | 武汉钢铁有限公司 | 800 MPa-grade multi-phase steel with good flanging performance and production method thereof |
| CN109554524B (en) * | 2018-11-28 | 2020-10-20 | 北京首钢冷轧薄板有限公司 | Technological control method for cold rolling production of 780 MPa-grade CP steel |
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| CN110747405A (en) * | 2019-10-24 | 2020-02-04 | 邯郸钢铁集团有限责任公司 | One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof |
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