Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained

The invention relates to a method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure. The inventive method consists in hot rolling a slab having a chemical composition which comprises, by weight, 0.01%≦C≦0.1%., 0.05%≦Mn≦1%, 0.01%≦Cr≦1%, 0.01%≦Si≦0.5%, 0.001%≦P≦0.2%, 0.01%≦Al≦0.1%, N≦0.01%, the remainder being iron and impurities resulting from the preparation thereof. The method also comprises the following subsequent steps consisting in: hot winding the band obtained at a temperature of between 550 and 850° C.; cold rolling the band with a reduction ratio of between 60 and 90%; annealing the band continuously in the intercritical region; cooling said band to ambient temperature, in one or more steps, the rate of cooling between 600° C. and ambient temperature being between 100° C./s and 1500° C/s; and, optionally, tempering same at a temperature of less than 300° C. The aforementioned annealing and cooling operations are performed such that the end band comprises between 1 and 15% martensite. The invention also relates to the steel band thus formed.

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Description
FIELD OF THE INVENTION

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.

PRIOR ART

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 Rm 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 is 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, which have a high mean anisotropy coefficient r but have only moderate mechanical properties, with a tensile strength Rm not exceeding 400 MPa.

As examples, mention may be made of low-interstitial 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.

SUMMARY OF THE INVENTION

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 at 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 Ac1 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 is a cold-rolled 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 Rm of greater than 450 MPa;

it has a tensile strength Rm of greater than 500 MPa;

it has a tensile strength Rm of greater than 600 MPa;

it has a mean anisotropy coefficient r of greater than 1.1;

it has a mean anisotropy coefficient r 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.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The process according to the invention consists in hot rolling a slab of specific composition and then in 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 coiling operation makes it possible for the Fe3C 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 is 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 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 is 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 averaging treatment, as is found in the prior art. This is because these averaging 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 in 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 to the invention includes 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.

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.

EXAMPLES

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.

C Mn Cr Si P Al N A 60 600 70 70 20 56 5 B 43 373 76 13 22 56 5.7

The balance of the compositions consists of iron and inevitable impurities resulting from the smelting.

ABBREVIATIONS EMPLOYED

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 AR3 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 temperature 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.

Tcoil Tsoak Rm Grade (° C.) (° C.) Direction Re (MPa) (MPa) P (%) r mean r % m A 720 800 T 420 711 0 1.10 0.98 14 L 405 713 0 1.11 45° 425 720 0 0.85 750 T 443 713 0 1.26 1.02 12 L 438 717 0 1.13 45° 451 736 0 0.84 B 720 800 T 432 656 0 1.46 1.27 8 L 430 697 0 1.60 45° 436 668 0 1.01 750 T 454 662 0 2.04 1.37 7 L 457 690 0 1.41 45° 461 677 0 1.01 550 800 T 455 677 0 1.47 1.21 6 L 446 667 0 1.44 45° 472 687 0 0.97 750 T 475 680 0.3 1.46 1.09 5 L 463 668 0.4 1.25 45° 482 697 0.3 0.83

The overall anisotropy of a steel is determined by the mean normal anisotropy coefficient r: r = r T + r L + 2 ⁢ r 45 4
where rT denotes the value of r measured in the direction transverse to the rolling direction of the strip, rL denotes the value of r measured in the longitudinal or rolling direction of the strip and r45° denotes the value of r measured at 45° to the rolling direction of the strip.

For a coiling temperature of 720° C., FIG. 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, FIG. 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

1. A process for producing a cold-rolled ferritic/martensitic dual-phase steel strip, wherein 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.

2. The process as claimed in claim 1, wherein 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, wherein the strip is hot rolled at a temperature above 850° C.

4. The process as claimed in any one of claims 1 to 3, wherein 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, wherein 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, wherein 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, wherein the soak temperature is between Ac1 and 900° C.

8. The process as claimed in claim 7, wherein the soak temperature is between 750 and 850° C.

9. The process as claimed in any one of claims 1 to 8, wherein 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 1 500° C./s, down to the ambient temperature.

10. The process as claimed in claim 9, wherein the second cooling step is carried out by water quenching.

11. The process as claimed in any one of claims 1 to 8, wherein 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, wherein 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, the chemical composition of which furthermore 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.

15. The steel strip as claimed in either of claims 13 and 14, which has a tensile strength Rm of greater than 450 MPa.

16. The steel strip as claimed in claim 15, which has a tensile strength Rm of greater than 500 MPa.

17. The steel strip as claimed in claim 16, further which has a tensile strength Rm of greater than 600 MPa.

18. The steel strip as claimed in any one of claims 13 to 17, which has a mean anisotropy coefficient r of greater than 1.1.

19. The steel strip as claimed in claim 18, further which 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, which furthermore contains between 1% and 10% martensite.

21. The steel strip as claimed in claim 20, which 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.

Patent History
Publication number: 20060144482
Type: Application
Filed: Jan 30, 2004
Publication Date: Jul 6, 2006
Inventor: Antoine Moulin (Metz)
Application Number: 10/544,206
Classifications
Current U.S. Class: 148/603.000
International Classification: C21D 8/02 (20060101);