ZA200505968B - Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained - Google Patents
Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained Download PDFInfo
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- ZA200505968B ZA200505968B ZA200505968A ZA200505968A ZA200505968B ZA 200505968 B ZA200505968 B ZA 200505968B ZA 200505968 A ZA200505968 A ZA 200505968A ZA 200505968 A ZA200505968 A ZA 200505968A ZA 200505968 B ZA200505968 B ZA 200505968B
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- South Africa
- Prior art keywords
- strip
- temperature
- cooling
- steel strip
- rolled
- Prior art date
Links
- 229910000734 martensite Inorganic materials 0.000 title claims description 33
- 238000000034 method Methods 0.000 title claims description 24
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 30
- 239000010959 steel Substances 0.000 claims description 30
- 238000001816 cooling Methods 0.000 claims description 22
- 239000000203 mixture Substances 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 16
- 238000003723 Smelting Methods 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 238000010791 quenching Methods 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 7
- 238000005496 tempering Methods 0.000 claims description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 230000000171 quenching effect Effects 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 238000005097 cold rolling Methods 0.000 claims description 3
- 238000010583 slow cooling Methods 0.000 claims description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- 239000011651 chromium Substances 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000011282 treatment Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- -1 aluminum nitrides Chemical class 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000002045 lasting effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009736 wetting Methods 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
-
- 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
-
- 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
- C21D2211/008—Martensite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
Description
Process for producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure, and band thus obtained
The present invention relates to a process for producing a cold-rolled ferritic/martensitic dual-phase steel strip and to a strip that can be obtained by this process, which is more particularly intended for the production of automobile parts by deep drawing.
Ultrahigh-strength steels have been developed in recent years, especially so as to meet the specific requirements of the automobile industry, which are in particular the reduction in weight, and therefore in thickness, of the parts and the improvement in safety afforded by the increase in fatigue strength and impact behavior of the parts. These improvements must also not degrade the formability of the steel sheet used for producing the parts.
Thus, dual-phase steels have been developed in which the structure is ferritic/martensitic, which make it possible to achieve a tensile strength Rn, of more than 400 MPa but which do not have good drawability characteristics, since their mean anisotropy coefficient r is close to 1. Moreover, their galvanizability 1s poor, since they contain large amounts of silicon or other elements deleterious to good wetting of the surface of the strip by the molten zinc.
Also known are steels with a single-phase structure, or which have a high mean anisotropy coefficient xr but have only moderate mechanical properties, with a tensile strength R, not exceeding 400 MPa.
As examples, mention may be made of low-interstitial
- 2 = steels and aluminum-killed reparkerized steels.
Attempts at enhancing the conventional hardening mechanisms for these types of steel fail to appreciably improve their mechanical properties. Furthermore, this steel must be capable of being galvanized.
The object of the present invention is to remedy the drawbacks of the steels of the prior art by proposing a steel strip capable of deep drawing and having at the same time excellent mechanical properties and excellent anisotropy characteristics.
For this purpose, the first subject of the invention is a process for producing a cold-rolled ferritic/martensitic dual-phase steel strip, characterized in that a slab, the chemical composition of which comprises, by weight: 0.010% < C £ 0.100% 0.050% < Mn < 1.0% 0.010% < Cr £ 1.0% 0.010% = Si < 0.50% 0.001% £ P <£ 0.20% 0.010% <£ Al £ 0.10%
N < 0.010% the balance being iron and impurities resulting from the smelting, is hot rolled, said process then comprising the steps consisting in: - coiling the hot-rolled strip obtained at a temperature of between 550 and 850°C; then - cold rolling the strip with a reduction ratio of between 60 and 90%; then - annealing the strip continuously in the intercritical range; and - cooling it down to the ambient temperature in one or more steps, the cooling rate between 600°C and the ambient temperature being between 100°C/s and 1500°C/s; and - optionally tempering it at a temperature below 300°C,
: the annealing and cooling operations being carried out in such a way that the strip finally contains from 1 to 15% martensite.
In a preferred method of implementation, the chemical composition of the steel furthermore comprises, by weight: 0.020% < C < 0.060% 0.300% < Mn < 0.500% 0.010% <£ Cr £ 1.0% 0.010% < Si £ 0.50% 0.010% <P < 0.100% 0.010% £ Al £ 0.10%
N < 0.010% the balance being iron and impurities resulting from the smelting.
The process according to the invention may also include the following features, by themselves or in combination: ~ the strip is hot rolled at a temperature above 850°C; - the strip is hot coiled al a temperature of between 550 and 750°C; - the strip is cold rolled with a reduction ratio of between 70 and 80%; - the continuous annealing of the cold-rolled strip comprises a temperature rise phase followed by a soak phase at a predetermined temperature; - the soak temperature is between Ac; and 900°C; - the soak temperature is between 750 and 850°C; - the cooling down to the ambient temperature comprises a first, slow cooling step between the soak temperature and 600°C, during which the cooling rate is ) less than 50°C/s, followed by a second cooling step at a higher rate, of between 100°C/s and 1500°C/s, down to the ambient temperature.
The second subject of the invention 1s a cold-rolled
. Ca : ferritic/martensitic dual-phase steel strip, the chemical composition of which comprises, by weight:
In a preferred embodiment, the composition of the strip is the following: 0.020% < C ££ 0.060% 0.300% £ Mn £ 0.500% 0.010% <£ Cr < 1.0% 0.010% £ Si < 0.50% 0.010% <P < 0.100% 0.010% £ Al < 0.10%
N <€ 0.010% the balance being iron and impurities resulting from the smelting.
The steel according to the invention may also include the following features, by themselves or in combination: - it has a tensile strength R,;, of greater than 450 MPa; - it has a tensile strength R, of greater than 500 MPa; - it has a tensile strength R, of greater than 600 MPa; - it has a mean anisotropy coefficient r of greater than 1.1; - it has a mean anisotropy coefficient rr of greater than 1.3; - it furthermore contains between 1% and 10% martensite; - it furthermore contains between 5% and 8% martensite.
Finally, the third subject of the invention is a steel strip according to the invention for the production of automobile parts by deep drawing.
The process according to the invention consists in hot rolling a slab of specific composition and then in
. Cs i! coiling the hot-rolled strip obtained at a temperature of between 550 and 850°C.
This high-temperature coiling operation is favorable to the development of what is called a texture, that is to say an anisotropic structure. This is because such a colling operation makes it possible for the FesC cementite precipitates to coalesce and to reduce the amount of carbon going back into solution during the anneal, this being detrimental to the development of the recrystallization texture.
The process then consists in cold rolling the strip with a reduction ratio of between 60 and 90% and then in annealing the strip continuously in the intercritical range.
The intercritical anneal allows most of the carbide phases formed during the coiling after the recrystallization to be redissolved. The fact that the austenization and the dissolution of the carbide phases take place after the recrystallization makes it possible to retain the carbon trapped during the recrystallization and to free it once the recrystallized ferrite texture has developed. The texture will therefore be unaffected by the carbon in solid solution, as 1s the case with low-temperature coiling, but is only impaired by the isotropic character of the martensite formed.
The process then consists in cooling the strip down to the ambient temperature, in one or more steps, the cooling rate between 600°C and the ambient temperature being between 100°C/s and 1500°C/s, and optionally in tempering it at a temperature below 300°C.
This rapid cooling step allows martensite to form in the structure of the steel, thereby achieving very good mechanical properties. However, measures must be taken
. Ce . to ensure that too much martensite does not form, as martensite is isotropic and therefore reduces the mean anisotropy coefficient r.
Water quenching allows substantial proportions of carbide phases to be formed in the composition in question. It 1s possible to reduce the amount of martensitic phase formed by lowering the soak temperature toward lower values in the intercritical range, or else by carrying out a slow cooling operation before the quench.
It is also possible to reduce the difference in hardness between the ferritic matrix and the martensitic phase, by cooling the strip more slowly or by performing a short tempering operation, lasting around one minute, on the martensitic phase formed after the water quench.
It should be noted that this tempering operation is in no case an overaging treatment, as 1s found in the prior art. This is because these overaging treatments, which are generally carried out between 300 and 500°C, have in particular the effect of suppressing the martensite, which is an essential element of the present invention. The tempering optionally carried out according to the invention consists 1n precipitating some of the carbon in solid solution trapped in the martensite, without reducing the proportion of this martensite. The maximum temperature of this tempering operation is 300°C, preferably 250°C and more particularly preferably 200°C.
The composition according toc the invention includes i carbon with a content of between 0.010% and 0.100%.
This element is essential for obtaining good mechanical properties but it must not be present in too great an amount, as it would cause an excessive proportion of martensitic phase to be formed.
. oo
It also includes manganese with a content of between 0.050% and 1.0%. Manganese improves the yield strength of the steel, but greatly reduces its ductility. This is why its content is limited.
The composition also includes chromium with a content of between 0.010% and 1.0%, which helps in the desired martensite formation.
The composition also includes silicon with a content of between 0.010% and 0.50%. This greatly improves the yield strength of the steel, but slightly reduces its ductility and degrades its coatability.
The composition also includes phosphorus with a content of between 0.001% and 0.20%, which hardens the microstructure without affecting its texture.
The composition also includes aluminum with a content of between 0.010% and 0.10%, which prevents aging by nitrogen trapping.
By way of nonlimiting examples, and so as to better illustrate the invention, two grades of steel were produced. Their compositions, in thousandths of a percent, are given in the following table.
RE RE NE ET Er. a | eo | evo | 70 [5 | 43 | 313] 76 | 13 | 22 | se [ 5.7
The balance of the compositions consists of iron and inevitable impurities resulting from the smelting.
Abbreviations employed
. Cg . Re: yield strength in MPa;
Rm: tensile strength in MPa; r: anisotropy coefficient;
P: plateau; $m: proportion of martensite.
After production, the two grades were austenized at 1250°C for one hour, so as to dissolve the aluminum nitrides. The slabs were then hot rolled in such a way that the end-of-rolling temperature was above 900°C, the value of AR; for both grades being about 870°C.
The hot-rolled strips were then cooled by water quenching, at a cooling rate of around 25°C/s, until the coiling temperature was reached. Grade A was coiled at 720°C, while one specimen of grade B was coiled at 550°C and another at 720°C.
The various specimens were then cold rolled so as to achieve a reduction ratio of 75%, then they underwent an annealing treatment at a soak temperature of 750°C in the case of some specimens and 800°C in the case of the others. The cooling down to the ambient Lemperature was then carried out at a rate of around 25°C/s by water quenching.
Next, the mechanical properties and the anisotropy characteristics of the steels obtained were measured.
The results are collated in the following table.
. Cs (°c) | (°c) (MPa) | (MPa) | (%) xr vr a2 [911 | 0 [1.10] s00 | tr [0s [713 | 0 [111]0.98) 1g as [as | 920 [ 0 Jo.6s] a | 720 vr [ass] 913 [ 0 [1.06] 750 | 1 43s | 117 | 0 |1a3]1.02) 12 asc [asi | 936 | 0 [0.64] v [a3 | ese | 0 [1.46] s00 | 1 | 430 | 607 | 0 [1.60]1.27 as | 436 | ees | 0 [1.01] 120 |r [asa | ee2 | 0 [2.04] 750 | 1 | a7 | eso | 0 [1.411.377 as> [ar | 69 | 0 [1.01] vr [ass [enn [0 [1.47] soo | 1 | ass [eer [0 [1.48)1.20 as° | 472 | 687 | 0 |0.07] 550 750 | 1 | 463 | ees [0.4 |1.25| 1.09]
The overall anisotropy of a steel is determined by the mean normal anisotropy coefficient r: rob thT2n, 4 where rr denotes the value of r measured in the direction transverse to the rolling direction of the strip, r; denotes the value of r measured in the longitudinal or rolling direction of the strip and rss denotes the value of r measured at 45° to the rolling direction of the strip.
For a coiling temperature of 720°C, figure 1 shows the relationship between the mean coefficient r and the content of martensite formed %m for grades A and B. It
. may be seen that the higher the martensite content, the more anisotropic the steel.
It may also be seen that the higher the martensite content, the higher the mechanical properties.
As an illustration, figure 2 shows the microstructure obtained with grade A, coiled at 720°C and then annealed at 750°C in order finally to obtain 12% martensite. The ferrite and the martensite formed can be clearly distinguished in the figure.
Claims (22)
1. A process for producing a cold-rolled ferritic/martensitic dual-phase steel strip, characterized in that a slab, the chemical composition of which comprises, by weight:
0.010% < C <£ 0.100%
0.050% £ Mn £ 1.0%
0.010% < Cr <£ 1.0%
0.010% < Si < 0.50%
0.001% £ P £ 0.20%
0.010% £ Al £ 0.10% N < 0.010% the balance being iron and impurities resulting from the smelting, is hot rolled, sald process then comprising the steps consisting in: - coiling the hot-rolled strip obtained at a temperature of between 550 and 850°C; then - cold rolling the strip with a reduction ratio of between 60 and 90%; then - annealing the strip continuously in the intercritical range; and - cooling it down to the ambient temperature in one or more steps, the cooling rate between 600°C and the ambient temperature being between 100°C/s and 1500°C/s; and - optionally tempering it at a temperature below 300°c, the annealing and cooling operations being carried out in such a way that the strip finally contains from 1 to 15% martensite.
2. The process as claimed in claim 1, characterized in that the chemical composition of the steel comprises:
0.020% < C £ 0.060%
0.300% < Mn < 0.500%
. 0.010% £ Cr £ 1.0%
0.010% < Si £ 0.50%
0.010% <P £ 0.100%
0.010% < Al <£ 0.10% N < 0.010% the balance being iron and impurities resulting from the smelting.
3. The process as claimed in either of claims 1 and 2, characterized in that the strip is hot rolled at a temperature above 850°C.
4. The process as claimed in any one of claims 1 to 3, characterized in that the strip is hot rolled at a temperature of between 550 and 750°C.
5. The process as claimed in any one of claims 1 to 4, characterized in that the strip is cold rolled with a reduction ratio of between 70 and 80%.
6. The process as claimed in any one of claims 1 to 5, characterized in that the continuous annealing of the cold-rolled strip comprises a temperature rise phase followed by a soak phase at a predetermined temperature.
7. The process as claimed in claim 6, characterized in that the soak temperature is between Ac; and 900°C.
8. The process as claimed in claim 7, characterized in that the soak temperature is between 750 and 850°C.
9. The process as claimed in any one of claims 1 to 8, characterized in that the cooling down to the a ambient temperature comprises a first, slow cooling step between the soak temperature and 600°C, during which the cooling rate is less than 50°C/s, followed by a second cooling step at a higher rate, of between 100°C/s and 1 500°C/s, down to the ambient temperature.
10. The process as claimed in claim 9, characterized in that the second cooling step is carried out by water quenching.
11. The process as claimed in any one of claims 1 to 8, characterized in that the cooling is carried out in a single operation at a cooling rate of between 100°C/s and 1500°C/s.
12. The process as claimed in claim 11, characterized in that the cooling is carried out by water quenching.
13. A cold-rolled ferritic/martensitic dual-phase steel strip, the chemical composition of which comprises, by weight:
0.010% £ C <£ 0.100%
0.050% < Mn < 1.0%
0.010% < Cr £ 1.0%
0.010% £ si <£ 0.50%
0.001% £ P £ 0.20%
0.010% £ Al <£ 0.10% N < 0.010% the balance being iron and impurities resulting from the smelting, the strip furthermore containing between 1% and 15% martensite.
14. The steel strip as claimed in claim 13, characterized in that its chemical composition furthermore comprises:
0.020% < C £ 0.060%
0.300% < Mn < 0.500%
0.010% < Cr £ 1.0%
0.010% < si £ 0.50% R
0.010% <P < 0.100%
0.010% <£ Al <£ 0.10% N < 0.010% the balance being iron and impurities resulting from the smelting.
15. The steel strip as claimed in either of claims 13 and 14, characterized in that it has a tensile strength Rn of greater than 450 MPa.
16. The steel strip as claimed in claim 15, characterized in that it has a tensile strength R, of greater than 500 MPa.
17. The steel strip as claimed in claim 16, further characterized in that it has a tensile strength Ry of greater than 600 MPa.
18. The steel strip as claimed in any one of claims 13 to 17, characterized in that it has a mean anisotropy coefficient r of greater than 1.1.
19. The steel strip as claimed in claim 18, further characterized in that it has a mean anisotropy coefficient r of greater than 1.3.
20. The steel strip as claimed in any one of claims 13 to 19, characterized in that it furthermore contains between 1% and 10% martensite.
21. The steel strip as claimed in claim 20, characterized in that it furthermore contains between 5% and 8% martensite.
22. The use of a steel strip as claimed in any one of claims 13 to 21 for the production of automobile parts by deep drawing.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR0301358A FR2850671B1 (en) | 2003-02-05 | 2003-02-05 | PROCESS FOR MANUFACTURING A DUAL-PHASE STEEL BAND HAVING A COLD-ROLLED FERRITO-MARTENSITIC STRUCTURE AND A BAND OBTAINED THEREFROM |
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Publication Number | Publication Date |
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ZA200505968B true ZA200505968B (en) | 2006-06-28 |
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ZA200505968A ZA200505968B (en) | 2003-02-05 | 2005-07-25 | Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained |
Country Status (16)
Country | Link |
---|---|
US (1) | US20060144482A1 (en) |
EP (1) | EP1592816B1 (en) |
JP (1) | JP4528769B2 (en) |
KR (1) | KR101091021B1 (en) |
CN (1) | CN100465299C (en) |
BR (1) | BRPI0407236A (en) |
CA (1) | CA2514736C (en) |
ES (1) | ES2831249T3 (en) |
FR (1) | FR2850671B1 (en) |
HU (1) | HUE052206T2 (en) |
MX (1) | MXPA05008189A (en) |
PL (1) | PL206109B1 (en) |
RU (1) | RU2341566C2 (en) |
UA (1) | UA87454C2 (en) |
WO (1) | WO2004079022A1 (en) |
ZA (1) | ZA200505968B (en) |
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Publication number | Priority date | Publication date | Assignee | Title |
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US7959747B2 (en) * | 2004-11-24 | 2011-06-14 | Nucor Corporation | Method of making cold rolled dual phase steel sheet |
US7442268B2 (en) * | 2004-11-24 | 2008-10-28 | Nucor Corporation | Method of manufacturing cold rolled dual-phase steel sheet |
US8337643B2 (en) | 2004-11-24 | 2012-12-25 | Nucor Corporation | Hot rolled dual phase steel sheet |
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2003
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- 2004-01-30 RU RU2005127577/02A patent/RU2341566C2/en active
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BRPI0407236A (en) | 2006-01-31 |
FR2850671B1 (en) | 2006-05-19 |
CA2514736C (en) | 2012-12-04 |
KR101091021B1 (en) | 2011-12-09 |
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CN100465299C (en) | 2009-03-04 |
CN1748039A (en) | 2006-03-15 |
PL377834A1 (en) | 2006-02-20 |
UA87454C2 (en) | 2009-07-27 |
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WO2004079022A1 (en) | 2004-09-16 |
FR2850671A1 (en) | 2004-08-06 |
RU2005127577A (en) | 2006-02-10 |
KR20050095782A (en) | 2005-09-30 |
US20060144482A1 (en) | 2006-07-06 |
JP2006520431A (en) | 2006-09-07 |
ES2831249T3 (en) | 2021-06-08 |
JP4528769B2 (en) | 2010-08-18 |
EP1592816B1 (en) | 2020-10-14 |
EP1592816A1 (en) | 2005-11-09 |
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