CN102822371A - Steel sheet with high tensile strength and superior ductility and method for producing same - Google Patents
Steel sheet with high tensile strength and superior ductility and method for producing same Download PDFInfo
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- CN102822371A CN102822371A CN2011800167339A CN201180016733A CN102822371A CN 102822371 A CN102822371 A CN 102822371A CN 2011800167339 A CN2011800167339 A CN 2011800167339A CN 201180016733 A CN201180016733 A CN 201180016733A CN 102822371 A CN102822371 A CN 102822371A
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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
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C21D2211/001—Austenite
Abstract
Disclosed is a steel sheet with high tensile strength and superior ductility having tensile strength of 700 - 900 MPa and capable of avoiding abrupt failure during press molding and method for producing the same. The steel sheet with high tensile strength and superior ductility is characterized by having a composition containing 0.5 - 1.5% C, 0.1% or less Si, 10 - 25% Mn, 0.1% or less P, 0.05% or less S, 0.1% or less Al, 3.0 - 8.0% Ni, 0.1% or less Mo, and 0.01% or less N (% by mass), with the remainder being Fe and unavoidable impurities and by having recrystallized austenite particles with an average particle diameter of 5 - 30 [mu]m or, further, a microstructure formed from another structure with an areal proportion of 1% or less.
Description
Technical field
The present invention relates to the automobile is that high-tensile steel, the particularly tensile strength of using in the industrial fields such as Transport Machinery of representative (TS) is good high-tensile steel and the method for manufacture thereof of ductility of 700 ~ 900MPa.
Background technology
In recent years, from suppressing the viewpoint of global warming, the output that reduces carbonic acid gas becomes urgent subject, more in the past than the fuel efficiency that required to improve automobile more consumingly.Therefore, thus positive active research realizes that through the high tensileization as the steel plate of body material the slimming of component parts makes the countermeasure of body lightening.But; The high tensileization of steel plate will cause the reduction of press formability inevitably; Therefore advanced the exploitation of the steel plate that has high tensile and good press formability simultaneously; In trolley part, adopt duplex structure's steel plate that constitutes by ferritic and martensite or various complex tissue steel plates such as retained austenite steel plate so far, played certain effect with phase change induction plasticity.
Recently, confirm that the discharge regulation of carbonic acid gas will be strict more soon, the lightweight target of vehicle body is High Level extremely.Therefore, for used TS as for the high parts of the shaping difficulty of the steel plate below the 540MPa in the past, also need slimming, the TS that strong request has with the equal press formability of existing steel plate is the high-tensile steel of 700 ~ 900MPa.
From such situation, studied the less application of high Mn austenitic steel in high-tensile steel of the application in the metal sheet starting material so far.Even high Mn austenitic steel at room temperature also with austenite as principal phase; Be utilized as non-magnetic steel or Cryogenic Steel in the past; But because austenitic twinning-induced plasticity demonstrates significant work hardening and high ductility; Therefore, proposed effectively to utilize the novel high ductibility high-tensile steel of this effect.
For example, the method for manufacture of a kind of trolley part of excellent processability with the high tensile hot-rolled steel sheet disclosed, wherein in the patent documentation 1; To have after steel disc that following steel forms is heated to more than 1100 ℃; With the total rolling rate of roughing and finish to gauge more than 90% and finishing temperature more than 800 ℃, final thickness of slab reach the mode of 1.1 ~ 5.0mm, finish continuously hot final rolling, then; Be cooled to below 650 ℃ with 10 ~ 100 ℃/second speed of cooling; Batch then, wherein, the steel of said steel disc consists of: in weight %; Contain below the C:1.0%, Si:0.01 ~ 2.50%, Mn:10 ~ 30%, sol.Al:0.001 ~ 0.10%, below the P:0.05%, below the S:0.05%, surplus is made up of iron and unavoidable impurities.
In addition; Light steel band of the good HS of a kind of cold formability or steel plate are disclosed in the patent documentation 2; Wherein, In quality %, have below the C:1.00%, Mn:7.00 ~ 30.00%, Al:1.00 ~ 10.00%, Si: surpass 2.50% and 8.00% below, Al+Si: surpass 3.50% and 12.00% below, B: surpass 0.00% and: less than 8.00%, Cu: less than 3.00%, N: less than 0.60%, Nb: less than 0.30%, Ti: less than 0.30%, V: less than 0.30%, P: less than 0.01% less than 0.01% and the Ni of any composition of conduct.
In addition; Disclose TS in the patent documentation 3 and surpassed 900MPa, TS * El (El: elongation at break) surpass the Fe-C-Mn series austenite hot-rolled steel sheet of 45000MPa% and TS surpasses 45000MPa% above 950MPa, TS * El Fe-C-Mn series austenite cold-rolled steel sheet; Has following composition: in weight %; Contain below C:0.5 ~ 0.7%, Mn:17 ~ 24%, Si:3%, below the Al:0.050%, below the S:0.030%, below the P:0.08%, below the N:0.1%; And as in the element below the optional Cr:1%, below the Mo:0.40%, below the Ni:1%, below the Cu:5%, below the Ti:0.50%, below the Nb:0.50%, below the V:0.50% one or more; Surplus is made up of Fe and unavoidable impurities; The recrystallize rate surpasses 75%, and the area occupation ratio of carbide is less than 1.5%, and the average austenite grain footpath is less than 18 μ m.
In addition, the method for manufacture of the good high Mn non-magnetic steel of a kind of local deformaton ability is disclosed, wherein in the patent documentation 4; After steel ingot or steel disc be heated to 1050 ~ 1250 ℃; Make finishing temperature be 900 ℃ and carry out hot rolling, said steel ingot or steel disc contain C:0.15 ~ 0.70 weight %, Si:0.10 ~ 3.00 weight %, Mn:12 ~ 30 weight %, Ti:0.01 ~ 0.10 weight %, and surplus is made up of Fe and unavoidable impurities; While is about the content of C and Mn; Satisfy 60 * C weight %+Mn weight % >=36 weight %, and about the amount of non-metallic inclusion, cleanliness factor is below 0.03%.
The prior art document
Patent documentation
Patent documentation 1: japanese kokai publication hei 4-259325 communique
Patent documentation 2: Japan special table 2004-521192 communique
Patent documentation 3: Japan special table 2006-528278 communique
Patent documentation 4: japanese kokai publication hei 5-171273 communique
Summary of the invention
Invent problem to be solved
But; For the high Mn austenitic steel plate of record in the patent documentation 1 ~ 4; The so-called plasticity wild effect of work hardening characteristic instabilityization takes place easily at high strain regions, therefore, burst ground fracture and the problem of necking down does not take place easily when existing in drawing.
The objective of the invention is to, provide the burst in the time of to avoid drawing to rupture, have good high-tensile steel and the method for manufacture thereof of ductility of the TS of 700 ~ 900MPa.
The method that is used to deal with problems
The inventor furthers investigate to achieve these goals repeatedly, and the result finds following opinion.
Burst fracture during i) for fear of drawing, need use the local elongation rate (l-El:local elongation) of the 13B test film mensuration of stipulating among the JIS Z2201 is more than 5%.
Be more than 5% in order to make l-El ii), adding the above Ni of 3 quality % is that the microstructure that the recrystallize austenite crystal more than the 5 μ m constitutes is effective with forming by median size.
The present invention is based on such opinion and accomplishes; Provide a kind of ductility good high-tensile steel; It is characterized in that having following one-tenth and be grouped into, in quality %; Contain below C:0.5 ~ 1.5%, Si:0.1%, Mn:10 ~ 25%, below the P:0.1%, below the S:0.05%, below the Al:0.1%, Ni:3.0 ~ 8.0%, below the Mo:0.1%, below the N:0.01%; Surplus is made up of Fe and unavoidable impurities, and has following microstructure, is the recrystallize austenite crystal of 5 ~ 30 μ m or is further counted other organizational compositions below 1% with area occupation ratio by median size.
High-tensile steel of the present invention for example can pass through the following steps manufacturing; After will having the Heating temperature of steel billet reheat to 1100 ~ 1300 that mentioned component forms ℃; Carry out hot rolling with the finishing temperature more than 800 ℃; Be cooled at least 600 ℃ in the TR below 800 ℃ with the speed of cooling more than 20 ℃/second, batch with the coiling temperature below 600 ℃.
After batching, further carry out descaling, anneal with 750 ~ 1050 ℃ annealing temperature; Cooling off with the speed of cooling more than 10 ℃/second at least 450 ℃ TR from annealing temperature; Perhaps, carry out descaling, cold rolling, then; With 750 ~ 1050 ℃ annealing temperature annealing, cool off with the speed of cooling more than 10 ℃/second in TR from annealing temperature at least 450 ℃.
That is, high-tensile steel of the present invention be after the hot rolling steel plate, with the steel plate behind the steel plate annealing after the hot rolling, with behind the cold-rolling of steel plate after the hot rolling and annealing after steel plate in any one steel plate.
The invention effect
According to the present invention, can make burst fracture in the time of to avoid drawing, have the good high-tensile steel of ductility of the TS of 700 ~ 900MPa.High-tensile steel of the present invention has good strength-ductility balanced, therefore, also can in the high parts of shaping difficulty, use, and is very suitable for the lightweight of body of a motor car.
Embodiment
About ductility of the present invention good high-tensile steel and method of manufacture thereof, below at length describe.Need to prove that " % " short of special instruction of the amount of expression composition then is meant " quality % ".
1) becomes to be grouped into
C：0.5~1.5%
C is the element necessary to the stabilization of austenite phase, also brings into play bigger effect for the high tensileization of steel.But C measured less than 0.5% o'clock, and the stabilization of austenite phase becomes insufficient, can not get good ductility.On the other hand, the C amount surpasses at 1.5% o'clock, and owing to separating out of carbide, ductility reduces.Therefore, making the C amount is 0.5 ~ 1.5%, preferably is 0.5 ~ 1.0%.
Below the Si:0.1%
Si can add the deoxidant element that is used for steel.But,, add to surpass 0.1% and can cause saturated, the subsurface defect that causes by the increase of inclusion of deoxidation effect and the increase of surface imperfection as the Si content in the steel.Therefore, making the Si amount is below 0.1%.Need to prove that in order to obtain deoxidation effect fully, preferably making the Si amount is 0.01 ~ 0.1%.
Mn：10~25%
Mn is to the necessary element of austenite stabilization mutually with C equally.But Mn measured less than 10% o'clock, and the stabilization of austenite phase is insufficient, can not get good ductility.On the other hand, the Mn amount surpasses at 25% o'clock, and the hot workability of steel reduces, the manufacturing property of infringement steel plate.Therefore, make the Mn amount be 10 ~ 25%, preferably be 15 ~ 25%.And then, for the ductility that stably realizes being brought by twinning-induced plasticity improves effect, preferably control C amount and Mn amount with the mode that satisfies following (1) formula.
32≤20×[C]+[Mn]≤36…(1)
Wherein, [C], [Mn] represent the content of C, Mn respectively.
As stated, C influences austenite stabilization mutually with Mn.The contriver studies the stabilization of austenite phase and material behavior, particularly TS * El equilibrated relation, finds C amount, the Mn amount scope in the application, and during satisfied (1) formula of C amount and Mn amount, particularly TS * El balance is good.Can think this be because, 20 * [C]+[Mn] be lower than (1) formula, promptly less than 32 o'clock, austenite is unstable mutually; Martensitic transformation takes place easily, on the other hand, 20 * [C]+[Mn] is higher than (1) formula, promptly above 36 o'clock; It is too high that stacking fault energy becomes, and twinning-induced plasticity is difficult to occur.
Below the P:0.1%
P content exceeds 0.1%, the steel is reduced Toughness.Therefore, making the P amount is below 0.1%, preferably to be below 0.05%.
Below the S:0.05%
The S amount surpasses at 0.05% o'clock, and the hot workability of steel reduces.Therefore, making the S amount is below 0.05%, preferably to be below 0.02%.More preferably below 0.01%.
Below the Al:0.1%
Al is the element that can add the deoxidation that is used for steel.But,, add to surpass 0.1% and can cause the subsurface defect saturated, that cause by the increase of inclusion of deoxidation effect and the increase of surface imperfection as the Al content in the steel.Therefore, making the Al amount is below 0.1%.Need to prove that in order to obtain deoxidation effect fully, preferably making the Al amount is 0.01 ~ 0.1%.
Ni：3.0~8.0%
Ni is most important in the present invention element, thereby has the effect that stabilization improves ductility that manifests that the stacking fault energy that makes steel increases, makes twinning-induced plasticity.Special, effective to the inhibition of the plasticity instabilityization of high strain regions, effective to the raising of the l-El of high Mn austenitic steel plate.In order fully to obtain such effect, need make the Ni amount is more than 3.0%.But the Ni amount surpasses at 8.0% o'clock, and this effect is saturated, causes the increase of manufacturing cost simultaneously.Therefore, make the Ni amount be 3.0 ~ 8.0%, preferably be 3.0 ~ 6.0%.
Below the Mo:0.1%
Mo is the element that the recrystallize that makes steel postpones, helps through the micro of austenite crystal the high tensileization of steel.In order to obtain such effect, the Mo amount is preferably more than 0.01%.But Mo amount surpasses at 0.1% o'clock, and TS surpasses 900MPa, high tensileization and ductility is significantly reduced exceedingly.Therefore, making the Mo amount is below 0.1%, preferably to be below 0.05%.
Below the N:0.01%
The N amount surpasses at 0.01% o'clock, and the ductility of steel reduces.Therefore, making the N amount is below 0.01%, preferably to be below 0.005%.
Surplus is Fe and unavoidable impurities.
2) microstructure
It is recrystallize austenite crystal or the further microstructure in other organizational compositions of area occupation ratio below 1% of 5 ~ 30 μ m that high-tensile steel of the present invention has by median size.Realize high ductibilityization for the twinning-induced plasticity that utilizes the austenite phase, needing microstructure is austenite one phase.In addition, in order to make or even high strain regions also stably shows twinning-induced plasticity, austenite crystal need for fully discharged internal strain can recrystal grain.And the median size of austenite crystal is difficult to generate mechanical twin at high strain regions, thereby causes the generation of plasticity wild effect during less than 5 μ m.Therefore, for high-tensile steel of the present invention, the median size that makes the recrystallize austenite crystal is more than the 5 μ m, preferably is more than the 10 μ m.On the other hand, when median size surpasses 30 μ m, be difficult to obtain desirable T S.Therefore, making the median size of recrystallize austenite crystal is below the 30 μ m.
Need to prove, for the such high Mn austenitic steel plate of the present invention, according to the speed of cooling after the speed of cooling after the hot rolling and the annealing, generate cementite or martensite and equate its hetero-organization beyond the recrystallize austenite crystal sometimes.In order stably to obtain high tensile and good ductility, preferably suppress the generation of its hetero-organization, but to organize overall area occupation ratio be about below 1% as long as its hetero-organization accounts for, and then can not damage the object of the invention as far as possible.That is, high-tensile steel of the present invention have by median size be the microstructure that constitutes of the recrystallize austenite crystal of 5 ~ 30 μ m, or further in area occupation ratio cementite or equal other tissues of martensite 1% below.High-tensile steel of the present invention has following microstructure, and the median size of recrystallize austenite crystal is that 5 ~ 30 μ m and this recrystallize austenite crystal account for steel plate to organize overall area occupation ratio be more than 99%.
Wherein, For the median size of recrystallize austenite crystal, with 1000 times to 5000 times multiplying power, the SEM that the tissue of thickness of slab 1/4 position of the rolling direction parallel cutting surfaces of steel plate is carried out a plurality of visuals field observes; And, try to achieve through image analysis with the identification of phases of analyzing through EBSD.In addition, through based on the length-to-diameter ratio of grain shape whether less than 2, judge whether to be recrystal grain, or further and use the intragranular dependent variable of analyzing through EBSD to infer and confirm.
3) create conditions
Below, preferably creating conditions of steel plate of the present invention is shown.Need to prove that the method for manufacture of high-tensile steel of the present invention is not limited to following method.
The Heating temperature of steel billet: 1100 ~ 1300 ℃
When the Heating temperature of steel billet surpassed 1300 ℃, hot workability reduced, and the heating energy needed increases.On the other hand, Heating temperature is during less than 1100 ℃, the increase of the load when causing hot rolling.Therefore, make the Heating temperature of steel billet be 1100 ~ 1300 ℃, preferably be 1150 ~ 1250 ℃.Need to prove that adding of steel billet pined for, can carry out reheat, also can the high steel billet of temperature in the process of cooling after the casting be heated auxiliaryly or be incubated the steel billet that is cooled to behind the normal temperature.
Finishing temperature during hot rolling: more than 800 ℃
When the finishing temperature during hot rolling was lower than 800 ℃, recrystallize and grain growing can not be carried out fully, obtain the hot-rolled steel sheet of remaining non-recrystallization crystal grain easily, and carry out causing under the cold rolling situation increase of rolling load afterwards.Finishing temperature when therefore, making hot rolling is more than 800 ℃, preferably is more than 850 ℃.On the other hand, when finishing temperature surpassed 1050 ℃, it is excessively thick that crystal grain becomes easily, and intensity and ductility reduce sometimes.Therefore, preferably making finishing temperature is below 1050 ℃.Need to prove,, also can utilize heating units such as strip edge heater or strip well heater, the steel plate in the auxiliary ground heating rolling in order to ensure finishing temperature.
Speed of cooling after the hot rolling: be more than 20 ℃/second in the TR below 800 ℃
After the hot rolling, when cooling off less than 20 ℃/second speed of cooling, cementite is separated out in cooling in the TR below 800 ℃, and ductility reduces.Therefore, after the hot rolling, need in the TR below 800 ℃, be cooled at least 600 ℃ with the speed of cooling more than 20 ℃/second.Need to prove that when the speed of cooling after the hot rolling surpassed 100 ℃/second, recrystallize was not accomplished sometimes, therefore, preferably making the speed of cooling after the hot rolling is below 100 ℃/second.
Need to prove that finishing temperature surpasses under 800 ℃ the situation, in order to promote recrystallize, also can in 800 ℃ TR, carry out 1 ~ 10 second naturally cooling (air cooling).Need to prove, under this situation, in the TR below 800 ℃, be cooled at least 600 ℃ with the speed of cooling more than 20 ℃/second.
Coiling temperature: below 600 ℃
When coiling temperature surpasses 600 ℃, generate cementite in the slow process of cooling after batching, cause the reduction of ductility.Therefore, making coiling temperature is below 600 ℃, preferably is below 550 ℃.
Steel plate after the hot rolling of making like this can be directly as high-tensile steel of the present invention, but also can under following annealing conditions, anneal behind the steel plate descaling after the hot rolling or with behind the steel plate descaling after the hot rolling and after cold rolling.Need to prove that descaling can carry out through ordinary methods such as pickling.
Annealing conditions: annealing temperature: 750 ~ 1050 ℃, from the speed of cooling of annealing temperature: more than 10 ℃/second up at least 450 ℃ TR
In order to promote the grain growing of the steel plate after the hot rolling, can under 750 ~ 1050 ℃ annealing temperature, anneal.More preferably under 800 ~ 1000 ℃ annealing temperature, anneal.
In addition, for the thickness of slab that obtains expecting, the steel plate after cold rolling to the enforcement of the steel plate after the hot rolling carries out under the annealed situation, need under 750 ~ 1050 ℃ annealing temperature, anneal.This is to be the microstructure that the recrystallize austenite crystal of 5 ~ 30 μ m constitutes for the tissue that makes steel plate forms by median size.When annealing temperature was lower than 750 ℃, recrystallize was not accomplished, and can not get sufficient ductility.On the other hand, when annealing temperature surpassed 1050 ℃, it is excessively thick that crystal grain becomes, and intensity and ductility reduce sometimes.More preferably under 800 ~ 1000 ℃ annealing temperature, anneal.Need to prove that cold rolling rolling rate be so long as can access the rolling rate of the thickness of slab of expectation and get final product, not special the qualification, but, preferably be about 50% ~ about 70% from the viewpoint of production efficiency.
No matter have or not cold rollingly, during less than 10 ℃/second, generate cementite up at least 450 ℃ speed of cooling from annealing temperature, ductility reduces.Therefore, need cool off with the speed of cooling more than 10 ℃/second up at least 450 ℃ TR from annealing temperature.
For melting steel of the present invention, can use in converter, the electric furnace any one.The steel of melting obtains steel billet through ingot casting-split rolling method or continuous casting like this.As required, preferably implement the surfacing etc. of various pre-treatment, secondary refining or steel billet.In addition, about annealing,, preferably implement through continuous annealing apparatus from the viewpoint of productivity.Even being implemented various plating, the steel plate after steel plate after the hot rolling or the annealing can not damage effect of the present invention yet.Can also implement to be used for the temper rolling of shape correction or reconciliation statement surface roughness to the steel plate after steel plate after the steel plate after the hot rolling, the annealing or the plating processing.In addition, can also implement various surface treatments such as application, coating to steel plate of the present invention.
Embodiment
The steel billet of steel A ~ K that one-tenth shown in the his-and-hers watches 1 is grouped into carries out hot rolling under the hot-rolled condition shown in the table 2; Obtain the hot-rolled steel sheet of thickness of slab 3mm; After removing descaling through pickling; Further under the annealing conditions shown in the table 2, anneal for a part of steel plate, or under cold rolling rate shown in the table 2 and annealing conditions, carry out cold rolling after annealing, make hot rolling after, hot rolling+annealing, cold rolling+annealed steel plate 1 ~ 20.
For the steel plate of making, investigate microstructure through aforesaid method, obtain the median size of formation, recrystallize austenite crystal mutually.Need to prove, in the table 3, about constituting mutually; Tissue beyond the recrystallize austenite crystal is observed in area occupation ratio under 1% the situation of surpassing; The kind of representing its hetero-organization is counted with area occupation ratio under the situation below 1% at its hetero-organization, expression recrystallize austenite.In addition, choose the 13B test film of stipulating among the JIS Z 2201,, implement tension test, obtain TS, El, l-El, TS * El according to the method for regulation among the JIS Z 2241 along rolling direction.Need to prove that TS * El is under the above situation of 60GPa%, is judged to be the good high-tensile steel of ductility.
The result is shown in table 3.It is the microstructure that the recrystallize austenite crystal more than the 5 μ m constitutes that the steel plate of the present invention's example all has by median size; TS is 700 ~ 900MPa; L-El is more than 5%; TS * El is more than the 60GPa%, can know the good high-tensile steel of ductility of the burst fracture in the time of can avoiding drawing.In addition, satisfy under the situation of above-mentioned (1) formula, can know that TS * El is good especially.
Table 1
(quality %)
Table 2
* below speed of cooling 1:800 ℃ up to the speed of cooling of coiling temperature
* speed of cooling 2: from the speed of cooling of annealing temperature up to 450 ℃
Table 3
※ Y: austenite, M: martensite
Claims (4)
1. high-tensile steel that ductility is good; It is characterized in that; Having following one-tenth is grouped into; In quality %, contain below C:0.5 ~ 1.5%, Si:0.1%, Mn:10 ~ 25%, below the P:0.1%, below the S:0.05%, below the Al:0.1%, Ni:3.0 ~ 8.0%, below the Mo:0.1%, below the N:0.01%, surplus is made up of Fe and unavoidable impurities; And have following microstructure, be the recrystallize austenite crystal of 5 ~ 30 μ m or further count other organizational compositions below 1% with area occupation ratio by median size.
2. the method for manufacture of the high-tensile steel that a ductility is good; It is characterized in that; After will having the Heating temperature of steel billet reheat to 1100 ~ 1300 that the described one-tenth of claim 1 is grouped into ℃; Carry out hot rolling with the finishing temperature more than 800 ℃, be cooled at least 600 ℃ with the speed of cooling more than 20 ℃/second, batch with the coiling temperature below 600 ℃ in the TR below 800 ℃.
3. the method for manufacture of the high-tensile steel that ductility as claimed in claim 2 is good; It is characterized in that; After batching; Further carry out descaling, anneal, cooling off with the speed of cooling more than 10 ℃/second up at least 450 ℃ TR from annealing temperature with 750 ~ 1050 ℃ annealing temperature.
4. the method for manufacture of the high-tensile steel that ductility as claimed in claim 2 is good; It is characterized in that; After batching, further carry out descaling, cold rolling, then; Annealing temperature with 750 ~ 1050 ℃ is annealed, and is cooling off with the speed of cooling more than 10 ℃/second up at least 450 ℃ TR from annealing temperature.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2010077305A JP5003785B2 (en) | 2010-03-30 | 2010-03-30 | High tensile steel plate with excellent ductility and method for producing the same |
| JP2010-077305 | 2010-03-30 | ||
| PCT/JP2011/055007 WO2011122237A1 (en) | 2010-03-30 | 2011-02-25 | Steel sheet with high tensile strength and superior ductility and method for producing same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102822371A true CN102822371A (en) | 2012-12-12 |
| CN102822371B CN102822371B (en) | 2015-05-20 |
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| Application Number | Title | Priority Date | Filing Date |
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| CN201180016733.9A Expired - Fee Related CN102822371B (en) | 2010-03-30 | 2011-02-25 | Steel sheet with high tensile strength and superior ductility and method for producing same |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP2554699B1 (en) |
| JP (1) | JP5003785B2 (en) |
| KR (1) | KR101287331B1 (en) |
| CN (1) | CN102822371B (en) |
| WO (1) | WO2011122237A1 (en) |
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| TWI630277B (en) * | 2016-12-19 | 2018-07-21 | 杰富意鋼鐵股份有限公司 | High manganese steel plate and manufacturing method thereof |
| CN110114491A (en) * | 2016-12-22 | 2019-08-09 | Posco公司 | Low-temperature flexibility and the excellent potassium steel and manufacturing method of yield strength |
| CN111051553A (en) * | 2017-09-01 | 2020-04-21 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
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- 2011-02-25 EP EP11762477.5A patent/EP2554699B1/en not_active Not-in-force
- 2011-02-25 CN CN201180016733.9A patent/CN102822371B/en not_active Expired - Fee Related
- 2011-02-25 KR KR1020127021879A patent/KR101287331B1/en active IP Right Grant
- 2011-02-25 WO PCT/JP2011/055007 patent/WO2011122237A1/en active Application Filing
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| JPH04259325A (en) * | 1991-02-13 | 1992-09-14 | Sumitomo Metal Ind Ltd | Production of hot rolled high strength steel sheet excellent in workability |
| JPH05171273A (en) * | 1991-12-26 | 1993-07-09 | Kobe Steel Ltd | Production of high mn nonmagnetic steel excellent in local deformability |
| CN1079513A (en) * | 1991-12-30 | 1993-12-15 | 浦项综合制铁株式会社 | Hadfield Steel and manufacturing process thereof with superior formability, intensity and weldability |
| CN1846002A (en) * | 2003-07-22 | 2006-10-11 | 于西纳公司 | Method of producing austenitic iron/carbon/manganese steel sheets having a high strength and excellent toughness and being suitable for cold forming, and sheets thus produced |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104711494A (en) * | 2015-04-14 | 2015-06-17 | 钢铁研究总院 | Low-density high-plasticity NiAl-reinforced ultrahigh-strength steel and preparation method thereof |
| TWI630277B (en) * | 2016-12-19 | 2018-07-21 | 杰富意鋼鐵股份有限公司 | High manganese steel plate and manufacturing method thereof |
| CN110114491A (en) * | 2016-12-22 | 2019-08-09 | Posco公司 | Low-temperature flexibility and the excellent potassium steel and manufacturing method of yield strength |
| CN110114491B (en) * | 2016-12-22 | 2021-09-10 | Posco公司 | High manganese steel having excellent low-temperature toughness and yield strength, and method for producing same |
| US11505853B2 (en) | 2016-12-22 | 2022-11-22 | Posco | High manganese steel having superior low-temperature toughness and yield strength and manufacturing method thereof |
| CN111051553A (en) * | 2017-09-01 | 2020-04-21 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
| CN111433381A (en) * | 2017-12-07 | 2020-07-17 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
| CN111433381B (en) * | 2017-12-07 | 2021-09-03 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
| CN111684093A (en) * | 2018-02-07 | 2020-09-18 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
| TWI716952B (en) * | 2018-08-03 | 2021-01-21 | 日商杰富意鋼鐵股份有限公司 | High Mn steel and its manufacturing method |
| US11959157B2 (en) | 2018-08-03 | 2024-04-16 | Jfe Steel Corporation | High-Mn steel and method of producing same |
| TWI726798B (en) * | 2019-08-21 | 2021-05-01 | 日商杰富意鋼鐵股份有限公司 | Steel and its manufacturing method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5003785B2 (en) | 2012-08-15 |
| WO2011122237A1 (en) | 2011-10-06 |
| EP2554699A1 (en) | 2013-02-06 |
| CN102822371B (en) | 2015-05-20 |
| KR20120113789A (en) | 2012-10-15 |
| JP2011208226A (en) | 2011-10-20 |
| KR101287331B1 (en) | 2013-07-23 |
| EP2554699B1 (en) | 2016-08-10 |
| EP2554699A4 (en) | 2015-07-08 |
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