Low density steel having good drawability

Abstract

A cold-rolled and annealed ferritic steel sheet is provided. The steel has a composition comprising, expressed by weight: 0.001C0.15%; Mn1%; Si1.5%; 7.5%AI10%; 0.020%Ti0.5%; S0.050%; and P0.1%.
A balance of the composition includes iron and inevitable impurities resulting from the smelting. The structure includes kappa () precipitates and equiaxed ferrite, an average grain size d of the equiaxed ferrite is less than 50 microns, and a linear fraction f of intergranular precipitates is less than 30%. The linear fraction f is defined by $f=\frac{{}_{\left(A\right)}\mathrm{di}}{{}_{\left(A\right)}\mathrm{Li}}.$
.sub.(A)di denotes the total length of grain boundaries containing precipitates relative to an area (A) and .sub.(A)Li denotes the total length of the grain boundaries relative to the area (A). A content of carbon in solid solution is less than 0.005% by weight, and the cold-rolled and annealed ferritic steel sheet has a thickness between 0.6 mm and 1.5 mm. A skin part or structural part for the automotive field is also provided.

Claims

1. A cold-rolled and annealed ferritic steel sheet, the steel has a composition comprising, expressed by weight: 0.001C0.15%; Mn1%; Si1.5%; 7.5%Al10%; 0.020%Ti0.5%; S0.050%; and P0.1%; a balance of the composition being iron and inevitable impurities resulting from the smelting; a structure of the steel comprises kappa () precipitates and equiaxed ferrite, an average grain size d of the equiaxed ferrite is less than 50 microns, and a linear fraction f of intergranular precipitates is less than 30%, the linear fraction f being defined by $f=\frac{{}_{\left(A\right)}\mathrm{di}}{{}_{\left(A\right)}\mathrm{Li}}$ .sub.(A)di denoting the total length of grain boundaries containing precipitates relative to an area (A) and .sub.(A)Li denoting the total length of the grain boundaries relative to the area (A); a content of carbon in solid solution is less than 0.005% by weight, and the cold-rolled and annealed ferritic steel sheet has a thickness from 0.6 mm to 1.5 mm.

2. The steel sheet according to claim 1, wherein the composition comprises, the contents being expressed by weight: 0.001%C0.010%; and Mn0.2%.

3. The steel sheet according to claim 1, wherein the composition comprises, the contents being expressed by weight: 0.010%C0.15%; and 0.2%Mn1%.

4. The steel sheet according to claim 1, wherein the composition comprises, the contents being expressed by weight 7.5%Al8.5%.

5. The steel sheet according to claim 1, wherein the steel has a ferritic matrix at all temperatures during manufacturing, from solidification after casting.

6. The steel sheet according to claim 1, the composition further comprising one or more elements, the contents being expressed by weight, selected from the group consisting of: Cr1%; Mo1%; Ni1%; Nb0.1%; V0.2%; and B0.010%.

7. The steel sheet according to claim 1, wherein the steel structure composition is homogenous.

8. The steel sheet according to claim 1, wherein a strength Rm is equal to or greater than 400 MPa.

9. The steel sheet according to claim 1, wherein a strength Rm is equal to or greater than 600 MPa.

10. A skin part or structural part in an automotive field comprising: a cold-rolled and annealed ferritic steel sheet according to claim 1.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) Other features and advantages of the invention will become apparent over the course of the description below, given by way of example and with reference to the figures appended herewith, in which:

(2) FIG. 1 defines schematically the linear fraction f of ferritic grain boundaries, in which there is intergranular precipitation;

(3) FIG. 2 shows the microstructure of a hot-rolled steel sheet according to the invention;

(4) FIG. 3 shows the microstructure of a hot-rolled steel sheet manufactured under conditions not complying with the invention;

(5) FIGS. 4 and 5 illustrate the microstructure of two cold-rolled and annealed sheets according to the invention; and

(6) FIG. 6 shows the microstructure of a cold-rolled and annealed steel sheet manufactured under conditions not complying with the invention.

DETAILED DESCRIPTION

(7) The present invention relates to steels having a reduced density, of less than about 7.3, while maintaining satisfactory usage properties.

(8) The invention relates in particular to a manufacturing process for controlling the precipitation of intermetallic carbides, the microstructure and the texture in steels containing especially particular combinations of carbon, aluminum and titanium.

(9) As regards the chemical composition of the steel, carbon plays an important role in the formation of the microstructure and in the mechanical properties.

(10) According to the invention, the carbon content is between 0.001% and 0.15%. Below 0.001%, significant hardening cannot be obtained. When the carbon content is above 0.15%, the cold rollability of the steels is poor.

(11) When the manganese content exceeds 1%, there is a risk of stabilizing the residual austenite at ambient temperature because of the propensity of this element to form the gamma-phase. The steels according to the invention have a ferritic microstructure at ambient temperature. Various particular methods of implementing the invention may be employed, depending on the carbon and manganese contents of the steel:

(12) When the carbon content is between 0.001 and 0.010% and when the manganese content is less than or equal to 0.2%, the minimum strength Rm obtained is 400 MPa; when the carbon content is greater than 0.010% but less than or equal to 0.15%, and when the manganese content is greater than 0.2% but less than or equal to 1%, the minimum strength obtained is 600 MPa.

(13) Within the carbon content ranges presented above, the inventors have demonstrated that this element contributes to substantial hardening by the precipitation of carbides (TiC or kappa precipitates) and by ferrite grain refinement. The addition of carbon results in only a small loss of ductility if the carbide precipitation is not intergranular or if the carbon is not in solid solution.

(14) Within these composition ranges, the steel has a ferrite matrix at all temperatures during the manufacturing cycle, that is to say right from solidification after casting.

(15) Like aluminum, silicon is an element allowing the density of the steel to be reduced. However, an excessive addition of silicon, above 1.5%, results in the formation of highly adherent oxides and the possible appearance of surface defects, leading in particular to a lack of wettability in hot-dip galvanizing operations. Furthermore, this excessive addition reduces the ductility.

(16) Aluminum is an important element in the invention. When its content is less than 6% by weight, a sufficient reduction in density cannot be obtained. When its content is greater than 10%, there is a risk of forming embrittling intermetallic phases Fe.sub.3Al and FeAl.

(17) Preferably, the aluminum content is between 7.5 and 10%. Within this range, the density of the sheet is less than about 7.1.

(18) Preferably, the aluminum content is between 7.5 and 8.5%. Within this range, satisfactory lightening is obtained without a reduction in ductility.

(19) The steel also contains a minimal amount of titanium, namely 0.020%, which helps to limit the content of carbon in solid solution to an amount of less than 0.005% by weight, thanks to the precipitation of TiC. Carbon in solid solution has a deleterious effect on the ductility because it reduces the mobility of dislocations. Above 0.5% titanium, excessive titanium carbide precipitation takes place, and the ductility is reduced.

(20) An optional addition of boron, limited to 0.010%, also helps to reduce the amount of carbon in solid solution.

(21) The sulphur content is less than 0.050% so as to limit any precipitation of TiS, which would reduce the ductility.

(22) For hot ductility reasons, the phosphorus content is also limited to 0.1%.

(23) Optionally, the steel may also contain, alone or in combination:

(24) chromium, molybdenum or nickel in an amount equal to or less than 1%. These elements provide additional solid-solution hardening;

(25) microalloying elements, such as niobium and vanadium in an amount of less than 0.1 and 0.2% by weight respectively, may be added in order to obtain additional precipitation hardening.

(26) The balance of the composition consists of iron and inevitable impurities resulting from the smelting.

(27) The structure of the steels according to the invention comprises a homogeneous distribution of highly disoriented ferrite grains. The strong disorientation between neighboring grains prevents the roping defect. This defect is characterized, during cold-forming of sheet, by the localized and premature appearance of strip in the rolling direction, forming a relief. This phenomenon is due to the grouping of recrystallized grains that are slightly disoriented, as they come from one and the same original grain before recrystallization. A structure sensitive to roping is characterized by a spatial distribution in the texture.

(28) When the roping phenomenon is present, the mechanical properties in the transverse direction (especially the uniform elongation) and the formability are greatly reduced. The steels according to the invention are insensitive to roping during forming, because of their favorable texture.

(29) According to one embodiment of the invention, the microstructure of the steels at ambient temperature consists of an equiaxed ferrite matrix, the average grain size of which is less than 50 microns. The aluminum is predominantly in solid solution within this iron-based matrix. These steels contain kappa () precipitates, which are an Fe.sub.3AlC.sub.x ternary intermetallic phase. The presence of these precipitates in the ferrite matrix results in substantial hardening. These precipitates must not however be present in the form of pronounced intergranular precipitation, as otherwise there would be a substantial reduction in ductility. The inventors have demonstrated that the ductility is reduced when the linear fraction of ferrite grain boundaries in which there is precipitation is equal to or greater than 30%. The definition of this linear fraction f is given in FIG. 1. If we consider a particular grain, the outline of which is bounded by successive grain boundaries of length L.sub.1, L.sub.2, . . . L.sub.i, the observations by microscopy show that this grain may have precipitates with a length d.sub.1, . . . d.sub.i along the boundaries. Considering an area (A) statistically representative of the microstructure, for example made up of more than 50 grains, the linear fraction of precipitates is given by the expression f:

(30) $f=\frac{{}_{\left[A\right]}{d}_i}{{}_{\left[A\right]}{L}_i}$
.sub.[A]d.sub.i denoting the total length of the grain boundaries containing precipitates relative to an area (A) in question and
.sub.[A]L.sub.i denoting the total length of the grain boundaries relative to said area (A) in question.

(31) The expression f therefore represents the degree to which the ferrite grain boundaries are covered with precipitates.

(32) According to another embodiment, the ferrite grain is not equiaxed but its average size d.sub.IV is less than 100 microns. The term d.sub.IV denotes the grain size measured by the method of linear intercepts over a representative area (A) perpendicular to the transverse direction with respect to rolling. The d.sub.IV measurement is carried out along the direction perpendicular to the thickness of the sheet. This non-equiaxed grain morphology, having an elongation in the rolling direction, may for example be present on hot-rolled steel sheets according to the invention.

(33) The method of implementing the process for manufacturing a hot-rolled sheet according to the invention is the following:

(34) a steel of composition according to the invention is supplied; and

(35) a semi-finished product is cast from this steel. This casting may be carried out in ingot form, or continuously in slab form with a thickness of around 200 mm. The casting may also be carried out in thin slab form, with a thickness of a few tens of millimeters, or in thin strip form, between counter-rotating steel rolls. This method of manufacture in the form of thin products is particularly advantageous as it makes it possible for a fine structure to be more easily obtained, conducive to implementing the invention as will be seen later. From his general knowledge, a person skilled in the art will be able to determine the casting conditions that meet both the need to obtain a fine equiaxed structure after casting and the need to meet the usual requirements of industrial casting.

(36) The cast semi-finished products are firstly heated to a temperature above 1150 C. so as to achieve, at all points, a temperature favorable to large deformations that the steel will undergo during the various rolling steps.

(37) Of course, in the case of direct thin slab or thin strip casting between counter-rotating rolls, the step of hot rolling these semi-finished products starting at above 1150 C. may be carried out directly after casting, so that an intermediate reheating step is in this case unnecessary.

(38) After many trials, the inventors have demonstrated that it is possible to prevent the problem of roping and to obtain very good drawability and good ductility, by means of the manufacturing process comprising the following steps:

(39) the semi-finished product is hot rolled by a succession of rolling steps in order to obtain a sheet.

(40) Each of these steps corresponds to a thickness reduction of the product by passing through rolls of the rolling mill. Under industrial conditions, these steps are carried out during the roughing of the semi-finished product on a strip mill. The reduction ratio associated with each of these steps is defined by the ratio (thickness of the semi-finished product after the rolling stepthickness before rolling)/(thickness before rolling). According to the invention, at least two of these steps are carried out at temperatures above 1050 C., the reduction ratio of each of them being equal to or greater than 30%. The time interval t.sub.i between each of the deformations with a ratio greater than 30% and the subsequent deformation is equal to or greater than 10 s so as to obtain complete recrystallization after this time interval t.sub.i. The inventors have demonstrated that this particular combination of conditions results in very considerable refinement of the hot-rolled structure. This thus promotes recrystallization thanks to rolling temperatures above the non-recrystallization temperature T.sub.nr.

(41) The inventors have also demonstrated that a fine initial structure, like that obtained after direct casting, is favorable to increasing the rate of recrystallization;

(42) the rolling is completed at a temperature T.sub.ER of 900 C. or higher, so as to obtain complete recrystallization;

(43) next, the sheet obtained is cooled. The inventors have demonstrated that particularly effective precipitation of precipitates and TiC carbides is obtained when the time interval t.sub.p that elapses when cooling from 850 to 700 C. is greater than 3 s. What is therefore obtained is intense precipitation favorable to hardening; and

(44) the sheet is then coiled at a temperature T.sub.coil of between 500 and 700 C. This step completes the precipitation of TiC.

(45) At this stage, a hot-rolled sheet is thus obtained that has a thickness of for example 2 to 6 mm. If it is desired to manufacture a sheet of smaller thickness, for example 0.6 to 1.5 mm, the manufacturing process is the following:

(46) a hot-rolled sheet, manufactured according to the process described above, is supplied. Of course, if the surface finish of the sheet so requires, a pickling operation is carried out by means of a process known per se;

(47) next, a cold-rolling operation is carried out, the reduction ratio being between 30 and 90%; and

(48) the cold-rolled sheet is then heated with a heating rate V.sub.h of greater than 3 C./s, so as to prevent restoration, which would reduce the subsequent recrystallizability. The reheating is carried out at an annealing temperature T, which would be chosen so as to obtain complete recrystallization of the highly work-hardened initial structure.

(49) The sheet is then cooled at a rate V.sub.c of less than 100 C./s so as not to cause any embrittlement by excess carbon in solid solution. This result is particularly surprising in so far as it might be considered that a rapid cooling rate would be favorable to reducing embrittling precipitation. Now, the inventors have demonstrated that slow cooling, at a cooling rate of less than 100 C./s, results in substantial carbide precipitation which thus reduces the content of carbon in solid solution. This precipitation has the effect of increasing the strength without a deleterious effect on the ductility.

(50) The annealing temperature T and the rate V.sub.c will be chosen so as to obtain, on the final product:

(51) complete recrystallization;

(52) a linear fraction f of intergranular precipitates of less than 30%; and

(53) a content of carbon in solid solution of less than 0.005%.

(54) A temperature T between 750 and 950 C. will be preferably chosen so as to obtain complete recrystallization. More particularly, when the carbon content is greater than 0.010% but less than or equal to 0.15%, and when the manganese content is greater than 0.2% but less than or equal to 1%, the temperature T will be chosen so as to furthermore prevent dissolution of the precipitates present before annealing. This is because, if these precipitates have dissolved, the subsequent precipitation on slow cooling will take place in embrittling intergranular form: too high an annealing temperature will result in redissolution of the precipitates formed during manufacture of the hot-rolled sheet and reduce the mechanical strength. For this purpose, it is preferable to choose a temperature T between 750 and 800 C.

(55) By way of non-limiting example, the following results will show the advantageous properties conferred by the invention.

Example 1

Hot-Rolled Sheet

(56) Steels were produced by casting them in the form of semi-finished products with a thickness of about 50 mm. Their compositions, expressed in percentages by weight, are given in Table 1 below.

(57) TABLE-US-00001 TABLE 1 Steel composition (wt %) Reference C Si Mn Al Ti Cr Mo Ni S P Nb I1 0.005 0.013 0.108 8.55 0.096 0.007 0.025 0.005 0.012 0.016 0.004 I2 0.009 0.013 0.108 8.5 0.097 0.008 0.027 0.005 0.013 0.016 0.005 I3 0.080 0.275 0.485 8.24 0.096 0.009 0.026 0.005 0.012 0.016 0.005 R1 0.010 0.170 0.09 6.8 0.006 0.032 0.005 0.001 0.009 R2 0.079 1.44 1.21 3.25 0.010 0.009 R3 0.005 0.010 0.010 14.5 0.104 0.010 0.009 R4 0.19 0.018 1.45 12.6 0.084 0.006 0.026 0.006 0.009 0.009 R5 0.197 0.010 1.7 10.2 0.010 0.009 R6 0.19 0.022 0.98 12.2 0.098 2.2 0.27 0.010 0.006 I = according to the invention; R = reference; underlined values = not according to the invention.

(58) The semi-finished products were reheated to a temperature of 1220 C. and hot rolled to obtain a sheet with a thickness of about 3.5 mm.

(59) Starting from the same composition, some of the steels were subjected to various hot-rolling conditions. The references I1-a, I1-b, I1-c, I1-d and I1-e denote for example five steel sheets manufactured under different conditions from the composition I1.

(60) In the case of steels I1 to I3, Table 2 details the conditions for the successive hot-rolling steps:

(61) the number N of rolling steps carried out at a hot-rolling temperature above 1050 C.;

(62) among these, the number N.sub.i of rolling steps for which the reduction ratio is greater than 30%;

(63) the time t.sub.i elapsing between each of the N.sub.i steps and the rolling step immediately following each of them;

(64) the end-of-rolling temperature TER;

(65) the time interval tp elapsing when cooling between 850 and 700 C.; and

(66) the coiling temperature Tcoil.

(67) TABLE-US-00002 TABLE 2 Manufacturing conditions during the hot-rolling T.sub.ER t.sub.p T.sub.coil Reference N N.sub.i t.sub.i (s) ( C.) (s) ( C.) I1a I 4 3 14.5 900 21 700 20.6 26.8 I1b R 6 2 2 900 21 700 2 I1c R 4 1 8 900 1.3 700 I1d I 5 3 26.5 900 21 700 23.5 20 I1e R 7 5 7.7 1050 20 700 5.2 3.5 3 2.5 I3a I 4 2 10 950 20 700 11 I3b R 4 1 5 950 20 700 I = according to the invention; R = reference; underlined values = not according to the invention.

(68) Table 3 shows the measured density on the sheets of Table 2 and certain mechanical and microstructural properties. Thus, the following were measured, in the transverse direction with respect to rolling: the strength Rm, the uniform elongation Au and the elongation at break At. Also measured was the grain size d.sub.IV using the method of linear intercepts according to the NF EN ISO 643 standard of a surface perpendicular to the transverse direction with respect to rolling. The dIV measurement was carried out along the direction perpendicular to the thickness of the sheet. For the purpose of obtaining enhanced mechanical properties, a grain size d.sub.IV of less than 100 microns is more particularly sought.

(69) TABLE-US-00003 TABLE 3 Properties of the hot-rolled sheets obtained from steels I1 and I3 Reference Rm (MPa) Au (%) At (%) Density D.sub.IV I1a I 505 10.7 25.4 7.05 75 I1b R 507 n.d n.d 7.05 200 I1c R 474 n.d n.d 7.05 450 I1d I 524 n.d n.d 7.05 40 I1e R 504 n.d n.d 7.05 120 I3a I 645 n.d n.d 7.07 70 I3b R 628 n.d n.d 7.07 400 I = aording to the invention; R = reference; n.d = not determined; underlined values = not aording to the invention.

(70) The steel sheets according to the invention, the microstructure of which is illustrated for example in FIG. 2 in the case of sheet I1d, are characterized by a grain size d.sub.IV of less than 100 microns and have a mechanical strength ranging from 505 to 645 MPa.

(71) Sheets I1b and I1e were rolled with too short an inter-pass time. Their structure is therefore coarse and non-recrystallized or insufficiently recrystallized, as shown in FIG. 3 relating to sheet I1e. Consequently, the ductility is reduced and the sheet is more sensitive to the roping defect. Similar conclusions may be drawn in the case of sheet I1b.

(72) Sheet I1c was rolled with an insufficient number of rolling steps with a reduction ratio greater than 30%, too short an inter-pass time and too short a time interval tp. The consequences are the same as those noted in the case of sheets I1b and I1e. Since the time interval t.sub.p is too short, hardening precipitation of precipitates and TiC carbides takes place only partially, thereby making it impossible to take full advantage of the hardening possibilities.

(73) The semi-finished products produced from the reference steels R1 to R6 were rolled so as to manufacture hot-rolled sheets under manufacturing conditions identical to those of steel I3a of Table 2. The properties obtained on these sheets are given in Table 4.

(74) TABLE-US-00004 TABLE 4 Mechanical properties of the hot-rolled sheets obtained from steels R1 to R6 Re Rm Au At Reference (MPa) (MPa) (%) (%) Density R1 n.d n.d. n.d. n.d. 7.2 R2 n.d. n.d. n.d. n.d. 7.44 R3 n.d. 450 0.1 0.1 6.48 R4 725 786 0.6 0.6 6.67 R5 596 687 2.7 2.7 6.9 R6 853 891 0.7 0.7 6.7 I = according to the invention; R = reference; n.d = not determined; underlined values = not according to the invention.

(75) Steel R1 possesses an insufficient titanium content, thereby leading to too high a content of carbon in solid solutionthe bendability is therefore reduced.

(76) Steel R2 possesses an insufficient aluminum content, thereby preventing a density of less than 7.3 being obtained.

(77) Steels R3, R4, R5 and R6 contain too high an amount of aluminum and possibly of carbon. Their ductility is reduced because of excessive precipitation of intermetallic phases or carbides.

Example 2

Cold-Rolled and Annealed Sheets

(78) Starting from hot-rolled steel sheets I1-a and I3-a (according to the invention) and I1-c and I3-b (not complying with the conditions of the invention), a cold-rolling operation was carried out with a reduction ratio of 75% in order to obtain sheets with a thickness of about 0.9 mm. The cold-rollability was noted during this step. Next, an annealing operation was carried out, characterized by a heating rate Vh=10 C./s. The annealing temperatures T and the cooling rates Vc are given in Table 5. Under these conditions, the annealing results in complete recrystallization.

(79) Starting from the same hot-rolled sheet, certain steels were subjected to various cold-rolling and annealing conditions. The references I3a1, I3a2, 13 a3 and I3a4 denote for example four steel sheets manufactured under different cold-rolling and annealing conditions from the hot-rolled sheet I3a.

(80) TABLE-US-00005 TABLE 5 Manufacturing conditions for cold-rolled and annealed sheets Cold- Reference rollability T V.sub.R I1a1 I Satisfactory 900 C. 13 C./s I1a2 R Satisfactory 900 C. 150C./s I1c1 R Satisfactory 900 C. 13 C./s I3a1 I Satisfactory 800 C. 13 C./s I3a2 R Satisfactory 800 C. 150C./s I3a3 R Satisfactory 900 C. 13 C./s I3a4 R Satisfactory 900 C. 150C./s I3b R Unsatisfactory (cracks in the transverse direction) I = according to the invention; R = reference; underlined values = not according to the invention.

(81) Table 6 shows certain mechanical, chemical, microstructural and density properties of the sheets of Table 5. Thus, the yield strength Re, the tensile strength Rm, the uniform elongation Au and the elongation at break At were measured by tensile tests in the transverse direction with respect to rolling. The possible presence of cleavage facets on the fracture surfaces of the test specimens was revealed by scanning electron microscope observations.

(82) The content of carbon in solid solution C.sub.sol was also measured, as were the bendability and drawability. The possible presence of roping following deformation was also revealed.

(83) The microstructure of these recrystallized sheets consisted of equiaxed ferrite, the average grain size d.sub. of which was measured in the transverse direction with respect to rolling. Also measured was the degree of coverage f of the ferrite grain boundaries with precipitates, by means of Aphelion image analysis software.

(84) TABLE-US-00006 TABLE 6 Mechanical properties of the cold-rolled and annealed sheets obtained from steels I1 and I3 Bendability Re Rm Au At Fracture C.sub.sol f and Reference (MPa) (MPa) (%) (%) mode d.sub. (%) (%) Roping drawability Density I1a1 I 390 497 18 31 Ductile 27 0.002 0 No Yes 7.05 I1a2 R 405 510 17 29 Ductile/brittle 27 0.005 0 n.d. Yes 7.05 I1c1 R 437 552 13.8 25 Ductile 53 n.d. n.d. Yes No 7.05 I3a1 I 531 633 16.5 28.8 Ductile 11 0.003 2 No Yes 7.07 I3a2 R 532 627 13.8 19 Ductile/brittle 11 0.010 0 No n.d. 7.07 I3a3 R 513 612 13 14 Ductile/brittle 12 n.d. 60 n.d. No 7.07 I3a4 R 613 687 12.8 16 Brittle 12 0.060 17 n.d. No 7.07 I = according to the invention; R = reference; n.d = not determined; underlined values = not according to the invention.

(85) Steel sheets I1a1 and I3a1 have a content of carbon in solid solution, an equiaxed ferrite grain size and a degree of coverage f of the grain boundaries that meet the conditions of the invention. Consequently, the bendability, the drawability and the roping resistance of these sheets are high.

(86) FIG. 4 illustrates the microstructure of steel sheet I1a1 according to the invention.

(87) FIG. 5 illustrates the microstructure of another steel sheet according to the invention, I3a1: note the presence of precipitates, only a small amount of which is present in intergranular form, thereby enabling a high ductility to be preserved.

(88) In comparison, steel sheet I1a2 was cooled at too high a rate after annealing: the carbon is then completely in solid solution, resulting in a reduction in ductility of the matrix manifested by the local presence of brittle areas on the fracture surfaces. Likewise, sheet I3a2 was cooled at too high a rate and also results in an excessive content in solid solution.

(89) FIG. 6 illustrates the microstructure of sheet I3a3, which was annealed at too high a temperature T: the precipitates present before annealing were dissolved and their subsequent precipitation upon cooling took place in excessive amount in an intergranular form. This results in the local presence of brittle areas on the fracture surfaces.

(90) Sheet I3a4 was also annealed at a temperature resulting in partial dissolution of the precipitates. The content of carbon in solid solution is excessive.

(91) Steel sheet I1c1 was manufactured from a hot-rolled sheet not complying with the conditions of the invention: the equiaxed grain size was too high, and the roping resistance and drawability were insufficient.

(92) Hot-rolled sheet I3b, not meeting the criteria of the invention, is incapable of deformation since transverse cracks appear during cold rolling.

(93) Spot resistance weldability trials were carried out on steel sheet I1a1, either in homogeneous welding (welding of two sheets of the same composition) or heterogeneous welding (welding with an interstitial-free steel sheet of the following composition, expressed in percentages by weight: 0.002% C, 0.01% Si; 0.15% Mn; 0.04% Al; 0.015% Nb; and 0.026% Ti). Examinations of the welded joints showed that they were defect-free.

(94) In the case of a subsequent heat treatment of the welded joints, the addition of 0.096% Ti guarantees the absence of carbon in solid solution in the heat-affected zone.

(95) The steels according to the invention exhibit good continuous galvanizability, in particular during an annealing cycle at 800 C. with a dew temperature above 20 C.

(96) The steels according to the invention therefore have a particularly advantageous combination of properties (density, mechanical strength, deformability, weldability, coatability). These steel sheets are used to advantage for the manufacture of skin or structural parts in the automotive field.