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CN103827338B - Low density high strength steel and method for producing said steel - Google Patents

Low density high strength steel and method for producing said steel Download PDF

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Publication number
CN103827338B
CN103827338B CN201280043488.5A CN201280043488A CN103827338B CN 103827338 B CN103827338 B CN 103827338B CN 201280043488 A CN201280043488 A CN 201280043488A CN 103827338 B CN103827338 B CN 103827338B
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Prior art keywords
steel sheets
steel
temperature
methods
band
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CN201280043488.5A
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CN103827338A (en
Inventor
刘成
R·罗纳
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Tata Steel Nederland Technology BV
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Tata Steel Nederland Technology BV
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    • 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
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates to a low density high strength steel sheet comprising 0.15% to 0.25% of C, 2.5% to 4% of Mn, 0.02% or less of P, 0. 015% or less of S, 6% to 9% of Al and 0.01% or less of N, the balance being iron and inevitable impurities, wherein 1.7*(Mn-Al) + 52.7*C is at least 3 and at most 4.5 and to a method of producing said low density and high strength steel sheet.

Description

Low-density and high-strength steel and the method preparing described steel
The present invention relates to low-density and high-strength steel sheets and be related to the method preparing low-density and high-strength steel sheets, for example With acting on the internal or external steel sheets of the constitutional detail of automobile.
Due to its excellent intensity and ductility and extremely low cost compared with aluminum or magnesium, allowed using more by exploitation The more strong grade of thin high strength steel sheet material, steel is generally used for making the car body of automobile lighter.However, in order to overcome future to weight The limitation reducing is it may be desired to using the substituting weight originated for reducing steel part.
There is more low-density steel be well known in the art.The TWIP steel with the high manganese content more than 20% is led Cause lighter steel matrix.Sometimes it is also added with the aluminum as lightweight element thus reducing the density of steel.It is used for adding at most 15% aluminum.
Known steel have a problem in that：Due to their tearing tendency and their high resistance to deformation in the operation of rolling Property, the processing characteristics of the existing equipment of steel industry is problematic.Other problems are welding sex chromosome mosaicism, especially for high alumina Content, and form the probability of unwanted martensite component.
It is an object of the present invention to provide can be using the low-density and high-strength steel of the existing equipment preparation of steel industry Sheet material.
It is a further object of the present invention to provide a kind of low-density with least relative low alloying of the intensity of 600MPa High strength steel sheet material.
It is a further object of the present invention to provide the method for preparing low-density and high-strength steel sheets.
One or more described by providing low-density and high-strength steel sheets as claimed in claim 1 to realize Purpose, described steel sheets comprise 0.15% to 0.25% C, 2.5% to 4% Mn, 0.02% or less P, 0.015% or less S, 6% to 9% Al and 0.01% or less N, surplus is ferrum and inevitable impurity, wherein 1.7 (Mn-Al)+52.7 C is at least 3 and is at most 4.5.Claim preferred embodiment in the dependent claims.
One or more described purposes are realized by the method for claim 7.Claiming in the dependent claims should The preferred embodiment of method.
The composition of the present invention is described more fully below（All consist of weight %）.
Carbon is used for producing cementite（Fe, Mn) 3C and Kappa carbide（Fe,Mn)3AlC.Carbon or stabilization of austenite unit Element, and provide dispersion-strengtherning by forming precipitate.Especially, due to columnar dendrite produced during continuously casting Faster recrystallization is to produce thick tissue, thus the formation of carbide is used for refining this tissue at high temperature.Additionally, adding 0.15% to 0.25% carbon is used for improving intensity.If however, the addition of carbon increases, cementite and Kappa carbide increase Amount be favorably improved intensity, but significantly reduce the ductility of steel.Particularly in the steel being added to aluminum, Kappa Carbide separates out on ferrite grain boundaries and causes fragility.Value less than 0.15% leads to too low intensity, and is higher than 0.25% Value tends to the risk improving to welding related problem, and therefore carbon content is 0.25 to the maximum.Preferably, carbon content is at least 0.16%th, more preferably at least 0.17%.Preferably, carbon content is at most 0.23, more preferably up to 0.20%.
Manganese contributes to forming austenite at high temperature together with carbon.Additionally, manganese increased the lattice paprmeter of steel thus reducing The density of steel.Find that the manganese of 2.5% minimum leads to significantly reducing of stable austenite and steel density.If however, manganese Amount be excessive, then center segregation leads in hot rolled sheet excessive band structure, and this causes the reduction of ductility. It is 4% therefore by the ceiling restriction of manganese.The preferred upper limit of manganese is 3.8%.
Phosphorus is the element being added with amount as few as possible.Phosphorus segregation cause red brittleness and cold brittleness on crystal boundary, thus The machinability of steel can be greatly reduced.The ceiling restriction of phosphorus is 0.02%, but preferably this amount is limited and be at most 0.01% Or even 0.005%.
Similar to phosphorus, sulfur promotes red brittleness.Especially, it produces thick MnS, MnS hot rolling and cold rolling when can cause Milled sheet is ruptured, and is therefore limited to 0.015% or lower.Preferably by sulfur content restriction at most 0.01% or even 0.005%.
Aluminum is the important element in the present invention together with carbon and manganese.Add the density that aluminum reduces steel.In view of proportion Reduce, preferably add substantial amounts of aluminum.Add 6% or more aluminum and lead to significantly reducing of steel density.If however, be excessively added Aluminum, then the amount increase of intermetallic compound such as Kappa carbide, FeAl or Fe3Al, this causes the ductility reduction of steel, leads to cold Cracking during rolling, is 9% therefore by ceiling restriction.Additionally, aluminum causes ductility-brittle transition temperature by less than zero degree Temperature near ambient temperature raising.Therefore, by the ceiling restriction of aluminum be 9%.The preferred lower limit of aluminum is 6.2%.
If adding substantial amounts of aluminum as in the present invention, nitrogen causes the formation of AlN precipitate.These precipitates are in post Shape dendrite refines and improves the ratio aspect of equiaxed dendrite is effective, and a small amount of nitrogen is favourable in steel for this reason 's.However, substantial amounts of nitrogen causes AlN precipitate that in a large number may be thick, this is unwanted.Therefore, the ceiling restriction of N is 0.01%.Preferably nitrogen quantity is limited and be at most 0.008% or even 0.005%.
Inventor finds, the steel in chemical composition range as explained above can not lead to show satisfactory Steel.If formula（1.7×(Mn-Al)+52.7C）Result be less than 3 or be higher than 4.5, then the ductility of the steel obtaining seems too Low.
By this formula, relatively control the amount of manganese and carbon to control ductility with the amount of aluminum.
In one embodiment, the composition selecting this steel sheets makes the value at least 1.3 and extremely of (36 C+Mn)/Al It mostly is 2.0.
In addition to the above-mentioned basic composition of the present invention, in order to improve or compensating intensity, ductility and other physical property of steel Matter, can also optionally add in the group being made up of to moderate Si, Cr, Mo, Ni, Cu, B, Ti, Zr, Nb, W and Ca on a small quantity One or two or more kinds of element.
Similar to aluminum, silicon also reduces the proportion of steel and contributes to the raising of intensity, but if be excessively added, then silicon can Produce thick, irregular high-temperature oxide film on the steel surface.Additionally, silicon causes brittle-ductile transition temperature by being less than The temperature of zero degree is to the higher improve of the ratio aluminum of near ambient temperature.Therefore, by the ceiling restriction of silicon be 2%.It is therefore preferable that silicon Amount be 0.1 to 2.0%.
Chromium is ferrite former, and it forms the Cr base carbide that can be used for refinement microstructure, and therefore this amount is permissible For 0.1% or higher.But if be excessively added, reduce ductility, it is 0.3% therefore by ceiling restriction.
Similar to chromium, molybdenum is the ferrite former forming fine carbides, and is added with 0.05% or higher amount.So And if be excessively added, it reduces the ductility of steel, therefore its upper limit is limited to 0.5%.
Nickel is austenite former, its can in the hot rolling introducing portion austenite to refine this tissue, thus Significantly improve anti-wrinkling property.However, the price of nickel is high and improves manufacturing cost, therefore by its boundary be limited to 0.1 to 2.0%.
The effect of copper is similar to nickel, but the price of usual copper is lower than nickel, and therefore it can be with 0.1% or higher scope Add.But if be excessively added, then caused by motlten metal its be present on crystal boundary with liquid condition cause intercrystalline Fragility, and cause crack at edge, therefore its amount is limited to 0.1 to 1.0%.
Boron limits ferritic Recovery and recrystallization in course of hot rolling, thus contributing to being led to by accumulative rolling reduction ratio Structure refinement and improve the intensity of steel, therefore this amount is 0.0005% or higher.But if be excessively added, then it can produce Boron-carbon compound, reduces the ductility of steel and deteriorates the wettability of galvanizing by dipping coating, by this ceiling restriction be therefore 0.003%.
Titanium forms Τ i Ν or TiC or the like, thus improves the crystal grain refinement of cast sturcture and contributes to Kappa carbonization The disperse of thing, therefore it is added with 0.01% or higher scope.However, titanium is expensive and improves manufacturing cost, and by In which reducing ductility by separating out intensity raising, it is 0.2% therefore by ceiling restriction.
The effect of zirconium is similar to titanium, and forms the nitride stronger with respect to titanium and carbide, therefore its with 0.005% or Higher scope is added.But zirconium is expensive, it is 0.2% therefore by ceiling restriction.
The effect of niobium is similar to titanium, and therefore it is added with 0.005% or higher scope.But different from titanium, niobium prolongs Late steel recrystallization at high temperature, thus drastically increases the rolling load of hot rolling.This makes it impossible to manufacture stalloy Material, is 0.2% therefore by ceiling restriction.
Tungsten is the heavy element improving steel proportion, therefore its interpolation（If added）In the range of 0.05 to 1.0%.Antimony （Sb）On crystal boundary, segregation limits the formation of Kappa carbide, therefore, antimony（If added）With 0.005% or higher scope Add.But if be excessively added, then its upper limit, to reduce ductility, is therefore limited to 0.2% by antimony segregation on crystal boundary.
Ca forms sulfide such as CaS and thus prevents the formation of MnS, therefore its with 0.001% or higher scope interpolation with Improve the hot-workability of steel.Ceiling restriction is 0.2%.
The steel sheets of the present invention include retained austenite tissue.This retained austenite compensate for the low of ferrite matrix structure Intensity simultaneously additionally aids the improvement of its ductility, and therefore based on area, the scope with 5% or higher includes retained austenite.Preferably Its upper limit is limited to 20%, more preferably this upper limit is 15% or even 12%.
The manufacture method of high intensity low-gravity steel sheets is described more fully below.
In order to manufacture the steel sheets of the present invention, heat slab first within the temperature range of 1000 to 1250 DEG C（I.e. thin plate Base (<150mm), heavy slab (150-400mm) or cast steel band (<20mm)）.If relation reheating temperature is more than 1250 DEG C, Form thick crystal grain in slab, it is possible to produce wrinkling and red brittleness, but if temperature is less than 1000 DEG C, then hot rolling essence Rolling temperature becomes too low so that it cannot manufacturing steel sheets and spraying to remove the oxidation film on high temperature surface using pressure (hydraulic) water, Thus cause surface defect.Therefore, relation reheating temperature is limited to 1000 to 1250 DEG C.Preferably, relation reheating temperature is at least 1100℃.
Due to implementing hot rolling at alap temperature thus effectively obtaining fine grain, thus according to the present invention, Implement finish rolling will pass through the dynamic or Static Recrystallization in course of hot rolling at a temperature of 900 DEG C or lower, preferably up to 850 DEG C Carry out crystal grain thinning.This means to be subjected to last hot deformation step when this material is at least in aforementioned temperature.But such as Really this temperature is too low, then deformation resistance improves and makes it difficult to manufacture steel sheets, and separates out Kappa carbide to provide elongation Structure, thus increases ridging defect, and therefore rolling temperature is 700 DEG C or higher, preferably 750 DEG C or higher and more preferably 800 DEG C or higher.
This hot-rolled steel band is wound under 600 DEG C or lower temperature.This temperature limiting roughening of crystallite dimension and card The excess of handkerchief carbide separates out.It also reduces being formed of the unusual coarsening crystal grain being caused by the secondary recrystallization of coarse grain Risk.Preferably coiling temperature is less than 550 DEG C.It is proved to cause in cold-rolled process sternly due to this material is quenched to ambient temperature Reopening is split, thus coiling temperature should be at least 200 DEG C, and is more preferably at least 300 DEG C.
Can with pickling and smooth and apply oil processing after the hot-finished material of gained is manufactured into hot-rolled steel sheet material.According to The present invention, this steel sheets is the low density steel sheet material with 7400kg/m3 or lower, the proportion of preferred 7300kg/m3 or lower.
Furthermore, it is possible to pickling and cold rolling after this hot-rolled steel sheet material is manufactured into cold rolling steel sheets.
In cold rolling, cold rolling reduction ratio is set to 40% or higher.If this is because cold rolling reduction ratio be set to 40% or Higher, then can fix the energy storing by cold working, and new recrystallized structure can be obtained.Preferably minimum cold rolling Lower rate is 50%.However, it is contemplated that production efficiency and economy, its upper limit is limited to 90% or lower.It is optionally possible to cold This material is made to stand intermediate annealing under roll compacting or between step.
In clean surface（If necessary）With continuous annealing or continuous hot-dipping galvanizing, this cold rolling steel sheets is processed afterwards. Selective annealing speed preferably in the range of 1 DEG C/s to 20 DEG C/s.If annealing rate is less than 1 DEG C/s, productivity ratio is too low, and And steel sheets are exposed to hot conditionss for a long time and thus cause grain coarsening and intensity decreases, deteriorate material quality.On the other hand, If more than 20 DEG C/s, due to insufficient remelting of carbide, thus the formation of austenite also becomes insufficient to annealing rate And therefore retained austenite reduces, thus reduce ductility.Cooldown rate after annealing is preferably 10 to 50 DEG C/s, or extremely Ambient temperature, or to zinc-plated bath and/or Wetted constructures.After zinc-plated or overaging, cooldown rate be preferably 10 to 50 DEG C/ S, more preferably 10 to 25 DEG C/s.
Implement annealing within the temperature range of between recovery temperature and 900 DEG C.In recovery temperature and less than recrystallization temperature Between, recover certain ductility.By selecting annealing temperature and time, this can be used for producing high strength steel simultaneously Guarantee sufficient ductility.Higher than recrystallization temperature and less than 900 DEG C, cold deformed microstructure easily recrystallizes.Can be easily true Surely the annealing temperature of perfect recrystallization of cold-rolled steel band and combining of annealing time are obtained.Inventor finds, if higher Annealing temperature under anneal this cold rolling material, then the austenite content in final products after annealing is relatively low.Higher than 900 DEG C, due to Form the austenite of relatively low amount, thus ductility reduction.Find that the suitable lower limit of annealing temperature is in the case of annealing steel 750℃.Preferably at least 800 DEG C of this lower limit.Carry out annealing 10 seconds or the longer intensity excellent with acquisition and processability.However, If annealing time was more than 180 seconds, the annealing process excessively reducing productivity ratio and extending can negatively affect property.
After annealing, by steel sheets be cooled to bath temperature and can by hot dip coating method micro- with its every side 10 to 200 The thickness of rice is coated with Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-Si, Al-Mg-Si etc., is consequently formed coated Steel sheets.These or other metal coat can also be applied by galvanoplastic.Painting preferably on this surface or each surface Thickness degree is 10 microns to 200 microns.
This material is preferably made to stand overaging after annealing.If be suitable for, can before hot dip coating process or it After carry out this overaging, this depend on factory design or depend on metallurgy preference.Overaging temperature be preferably 350 to 500 DEG C, and it is preferably from about 400 DEG C.The overaging time is more preferably at least 30 and/or is at most 180 seconds.In such overaging In the case of process, more preferably at least 825 DEG C and/or preferably up to 875 DEG C of annealing temperature.
In steel sheets prepared above, carbide and 5% or more retained austenite are dispersed in ferrite substrate, Tensile strength is made to be up to 600 to 900MPa, ductility is excellent, and the combination of therefore strength-ductility is also very excellent.One Plant in preferred embodiment, this steel sheets has the tensile strength of 600 to 900MPa.
The present invention will be described with reference to the following example in detail.Described embodiment for illustration purposes, and is not intended as to appoint Where formula limits the scope of the present invention.
Manufacture the steel sheets base with composition shown in table 1, at 1200 DEG C（RHT）Under heat again, and in 900 DEG C of finish rolling temperature The lower hot rolling of degree.The thickness of hot-rolled steel sheet material is 3 millimeters, and at 400 DEG C or 650 DEG C（S3）（Referring to table 2）Temperature（CT）Under Wind this hot-rolled steel sheet material.Inventor finds, in lower temperature（But it is higher than 700 DEG C）As the hot finishing at 850 DEG C does not affect this The microscopic structure of steel or property, but only roll-force is had an impact, this roll-force improves with the reduction of rolling temperature. However, it is possible to easily overcome the roll-force of this raising by using the milling train of suitable power.
Subsequently with 67% reduction ratio（CRR）This steel is made to stand cold rolling and in 800 to 1050 DEG C of annealing temperature（AT）Lower company Continuous annealing（Referring to table 3）, and carry out or do not carry out the overaging at 400 DEG C（Referring to table 4）.Annealing time be 60 seconds and The overaging time is 80 seconds.
Table 1- chemical composition
Sequence number C Al Mn Si P S N 1.7*(Mn-Al)+52.7*C
S1 0.18 6.7 3.4 0.01 0.004 0.003 0.005 3.90
S2 0.13 9.1 5.4 0.01 0.003 0.004 0.006 0.60
S3 0.004 6.8 0.02 0.01 0.004 0.005 0.004 -11.30
S1* 0.17 7.0 3.6 0.01 0.004 0.003 0.004 3.18
S1** 0.19 8.0 3.9 0.01 0.004 0.003 0.005 3.05
Table 2- technological parameter and engineering propertiess（YS：Yield strength in terms of MPa, TS：Tensile strength in terms of MPa, EI： Elongation percentage in terms of %, RA：Retained austenite in terms of volume %）
The impact of table 3- annealing temperature in the case of not having overaging
The impact of the combination of table 4- annealing temperature and overaging temperature
The result of S1 when the result of steel S1* and S1** is processed similar to such as S1.
It is obvious that recrystallizing in annealing process is constantly present balance and the amount of retained austenite between.Annealing temperature is got over Height, the amount of retained austenite is lower.
Wetted constructures are combined with higher anneal temperature and seem with beneficial effect.

Claims (20)

1. low-density and high-strength steel sheets, its comprise 0.15% to 0.19% C, 2.5% to 4% Mn, 0.02% or less P, 0.015% or less S, 6% to 9% Al and 0.01% or less N, optionally comprise selected from 0.1% to 2.0% Si, 0.1% to 0.3% Cr, 0.05% to 0.5% Mo, 0.1% to 2.0% Ni, 0.1% to 1.0% Cu, 0.0005% to 0.003% B, 0.01% to 0.2% Ti, 0.005% to 0.2% Zr, 0.05% to 1.0% W, One of 0.001% to 0.2% Ca or two or more elements, surplus is ferrum and inevitable impurity, wherein 1.7 (Mn-Al)+52.7 C is at least 3 and is at most 4.5.
2. in steel sheets as claimed in claim 1, wherein this sheet material, the amount of retained austenite is 5% or higher.
3. the steel sheets as any one of claim 1 to 2, the density of wherein this steel sheets is at most 7400kg/m3.
4. the steel sheets as any one of claim 1 to 2, wherein provide coat on one or both major surfaces, Wherein this coat is selected from Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-Si and Al-Mg-Si, and wherein in this master Coating layer thickness on surface or each first type surface is 10 microns to 200 microns.
5. steel sheets as any one of claim 1 to 2, the wherein value of (36 C+Mn)/Al at least 1.3 and at most For 2.0.
6. steel sheets as claimed in claim 3, the density of wherein this steel sheets is at most 7300kg/m3.
7. steel sheets as claimed in claim 3, wherein this steel sheets have the tensile strength of 600 to 900MPa.
8. the method preparing low-density and high-strength steel sheets, described steel sheets comprise 0.15% to 0.19% C, 2.5% to 4% Mn, 0.02% or less P, 0.015% or less S, 6% to 9% Al and 0.01% or less N, optionally comprise Si selected from 0.1% to 2.0%, 0.1% to 0.3% Cr, 0.05% to 0.5% Mo, 0.1% to 2.0% Ni, 0.1% to 1.0% Cu, 0.0005% to 0.003% B, 0.01% to 0.2% Ti, 0.005% to 0.2% Zr, One or two or more kinds of element of 0.1% to 1.0% W and 0.001% to 0.2% Ca, surplus is ferrum and can not keep away The impurity exempted from, wherein 1.7 (Mn-Al)+52.7 C is at least 3 and is at most 4.5, and the method comprises the following steps：
- plate slab, sheet billet or the band with above-mentioned chemical composition is provided；
- prepare slab or band for hot rolling by heating described slab or band in the range of 1000 DEG C to 1250 DEG C again Material；
- make this slab or band stand final hot finishing step, in the operation of rolling, the band of rolling has 700 DEG C to 900 DEG C Temperature；With
- after rolling, wind this hot-rolled band under 600 DEG C or lower temperature.
9. method as claimed in claim 8, the method is further comprising the steps：
- with 40% to 90% cold rolling reduction ratio this hot-rolled steel slab cold rolling or band to prepare cold-rolled steel band；
- under 900 DEG C of maximum temperature with the annealing rate of 1 to 20 DEG C/s by this cold-rolled steel band continuous annealing 10 to 180 seconds.
10. method as claimed in claim 9, wherein continuous annealing process are recovery annealings.
11. methods as claimed in claim 9, wherein continuous annealing process are recrystallization annealing.
In 12. methods as any one of claim 8 to 11, wherein this steel sheets the amount of retained austenite be 5% or Higher.
13. methods as any one of claim 8 to 11, the wherein value of (36 C+Mn)/Al at least 1.3 and at most For 2.0.
14. methods as any one of claim 9 to 11, wherein after annealing process on one or both major surfaces There is provided coat, wherein this coat is selected from Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-Si and Al-Mg-Si.
15. methods as any one of claim 9 to 11, wherein this annealing process include overage step.
16. methods as claimed in claim 15, wherein overage step be at a temperature of 350 to 500 DEG C and continue 30 to The time period of 180 seconds.
17. methods as claimed in claim 15, wherein annealing temperature are at least 825 DEG C and/or are at most 875 DEG C.
18. methods as any one of claim 9 to 11, the wherein combination of annealing temperature and annealing time be enough to obtain The perfect recrystallization of cold-rolled steel band.
19. methods as claimed in claim 18, wherein annealing temperature are 750 DEG C or higher.
20. methods as claimed in claim 14, the wherein coating layer thickness on this first type surface or each first type surface are 10 microns To 200 microns.
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