PRODUCTION METHOD FOR A SPOT WELDED JOINT USING HIGH STRENGTH AND HIGH FORMING STEEL

Abstract

A spot welded joint of at least two steel sheets is provided. At least one of the steel sheets presents yield strength above or equal to 600 MPa, an ultimate tensile strength above or equal to 1000 MPa, uniform elongation above or equal to 15%. The base metal chemical composition includes 0.05≤C≤0.21%, 4.0≤Mn≤7.0%, 0.5≤Al≤3.5%, Si≤2.0%, Ti≤0.2%, V≤0.2%, Nb≤0.2%, P≤0.025%, B≤0.0035%, and the spot welded joint contains a molten zone microstructure containing more than 0.5% of Al and containing a surface fraction of segregated areas lower than 1%, said segregated areas being zones larger than 20 μm.sup.2 and containing more than the steel nominal phosphorus content.

Claims

1. A method to permit production of a spot welded joint of at least two steel sheets, comprising the following steps: casting an aluminum alloyed steel so as to obtain a slab, a composition of the aluminum alloyed steel comprising, by weight percent: 0.05≤C≤0.21%; 4.0≤Mn≤7.0%; 0.5≤Al≤3.5%; P≤0.025%; and B≤0.0035%; reheating the slab at a temperature T.sub.reheat between 1150° C. and 1300° C.; hot rolling the reheated slab with a temperature between 800° C. and 1250° C. to obtain a hot rolled steel, a last hot rolling pass taking place at a temperature T.sub.lp greater than or equal to 800° C.; cooling the hot rolled steel between 1 and 150° C./s until a coiling temperature T.sub.coiling less than or equal to 650° C. is reached; then coiling the hot rolled steel cooled at T.sub.coiling; de-scaling; cold rolling with a cold rolling ratio between 30% and 70% so as to obtain a cold rolled steel sheet; heating at a heating rate H.sub.rate at least equal to 1° C./s up to an annealing temperature T.sub.anneal; annealing at the annealing temperature T.sub.anneal between T.sub.min and T.sub.max defined by:
T.sub.min=721−36*C−20*Mn+37*Al+2*Si (in ° C.), and
T.sub.max=690+145*C−6.7*Mn+46*Al+9*Si (in ° C.),  during a time between 30 and 700 seconds; cooling down to a targeted temperature at a cooling rate between 5° C./s and 70° C./s; and cutting the cold rolled steel into sheets to obtain cold rolled steel sheets; providing at least one of the cold rolled steel sheets to be welded in a welding process, the welding process including welding to another metal with an effective intensity between 3 kA and 15 kA and a force applied on the electrodes between 150 and 850 daN, an electrode active face diameter being between 4 and 10 mm.

2. The method to permit production of a spot welded joint as recited in claim 1 wherein the steps are performed successively.

3. The method to permit production of a spot welded joint as recited in claim 1 wherein the hot rolled steel sheet is batch annealed between 400° C. and 600° C. between 1 and 24 hours.

4. The method to permit production of a spot welded joint as recited in claim 1 wherein the hot rolled steel sheet is continuously annealed between 650° C. and 750° C. between 20 and 180 s.

5. The method to permit production of a spot welded joint as recited in claim 1 wherein the casting is done using a thin slab casting machine to obtain the hot rolled steel sheet.

6. The method to permit production of a spot welded joint as recited in claim 1 wherein the targeted temperature is a temperature T.sub.OA between 350° C. and 550° C. and kept at T.sub.OA for a time between 10 and 300 seconds.

7. The method to permit production of a spot welded joint as recited in claim 1 wherein the steel sheet is further cooled down to room temperature at a cooling rate V.sub.cooling3 above 5° C./s and below 70° C./s to obtain a cold rolled and annealed steel sheet.

8. The method to permit production of a spot welded joint as recited in claim 1 further comprising the step of: tempering the steel sheet at a temperature T.sub.temper between 170 and 400° C. for a time t.sub.temper between 200 and 800 s.

9. The method to permit production of a spot welded joint as recited in claim 1 further comprising the step of: coating the cold rolled steel sheet with Zn or a Zn alloy, after the step of annealing.

10. The method to permit production of a spot welded joint as recited in claim 1 further comprising: coating the cold rolled steel sheet with Al or an Al alloy, after the step of annealing.

11. The method to permit production of a spot welded joint as recited in claim 1 further comprising the step of: applying a post thermal treatment with an intensity between 60% and 90% of welding intensity for a time between 0.1 and 2 seconds.

12. The method as recited in claim 1 wherein the aluminum alloyed steel sheet further comprises, by weight percent: Si≤2.0%; Ti≤0.2%; V≤0.2%; Nb≤0.2%; and S≤0.004%; a balance of the composition being iron and unavoidable impurities resulting from smelting.

13. The method to permit production of a spot welded joint as recited in claim 1 wherein the spot-welded joint comprises: a molten zone microstructure including more than 0.5% of Al; and a surface fraction of segregated areas lower than 1%, the segregated areas being zones larger than 20 μm.sup.2 and including an amount of phosphorous greater than an aluminum alloyed steel nominal phosphorus content.

14. A method to permit production of a spot welded joint, at least one aluminum alloyed steel sheet being connected to the spot welded joint, the at least one aluminum alloyed steel sheet including a nominal phosphorus content; the at least one aluminum alloyed steel sheet having: a yield strength above or equal to 600 MPa; an ultimate tensile strength above or equal to 1000 MPa; and uniform elongation above or equal to 15%; and the spot-welded joint including: a molten zone microstructure including more than 0.5% of Al; and a surface fraction of segregated areas lower than 1%, the segregated areas being zones larger than 20 μm.sup.2 and including an amount of phosphorous greater than the nominal phosphorus content, the method comprising: providing the aluminum alloyed steel sheet to be welded to produce the spot-welded joint including the molten zone microstructure including more than 0.5% of Al and the surface fraction of segregated areas lower than 1%, the segregated areas being zones larger than 20 μm.sup.2 and including an amount of phosphorous greater than the nominal phosphorus content.

15. The method as recited in claim 14 wherein the aluminum alloyed steel sheet comprises, by weight percent: 0.05≤C≤0.21%; 4.0≤Mn≤7.0%; 0.5≤Al≤3.5%; P≤0.025%; and B≤0.0035%.

16. The method as recited in claim 15 wherein the aluminum alloyed steel sheet further comprises, by weight percent: Si≤2.0%; Ti≤0.2%; V≤0.2%; Nb≤0.2%; and S≤0.004%; a balance of the composition being iron and unavoidable impurities resulting from smelting.

17. A method to permit production of a spot welded joint for connecting at least two steel sheets, the spot-welded joint including a molten zone microstructure including more than 0.5% of Al; and a surface fraction of segregated areas lower than 1%, the segregated areas being zones larger than 20 μm.sup.2 and including an amount of phosphorous greater than an aluminium alloyed steel nominal phosphorus content, the method comprising: providing at least one sheet being made of an aluminum alloyed steel to be welded to produce the spot welded joint, the aluminum alloyed steel sheet comprising, by weight percent: 0.05≤C≤0.21%; 4.0≤Mn≤7.0%; 0.5≤Al≤3.5%; P≤0.025%; and B≤0.0035%; the at least one aluminum alloyed steel sheet having: a yield strength above or equal to 600 MPa; an ultimate tensile strength above or equal to 1000 MPa; and uniform elongation above or equal to 15%; a microstructure of the at least one aluminum alloyed steel sheet including from 20% to 50% of austenite, from 40% to 80% of annealed ferrite and less than 25% of martensite.

18. The method as recited in claim 17 wherein the aluminum alloyed steel sheet further comprises, by weight percent: Si≤2.0%; Ti≤0.2%; V≤0.2%; Nb≤0.2%; and S≤0.004%; a balance of the composition being iron and unavoidable impurities resulting from smelting.

Description

BRIEF DESCRIPTION

[0060] Other features and advantages of the invention will appear through the following detailed description. The figures joined are given by way of examples and shall not be taken as limiting the scope of the present invention. They are such that:

[0061] FIG. 1 illustrates the evolution of the hardness of hot rolled materials B1, C1, E1 and F1;

[0062] FIG. 2 illustrates the tensile properties of hot rolled materials B1, C1, E1 and F1;

[0063] FIG. 3 illustrates the tensile properties of cold rolled materials B1, C1, E1 and F1 before annealing;

[0064] FIG. 4A shows the tensile properties of cold rolled and annealed materials B1, C1, E1 and F1;

[0065] FIG. 4B shows the tensile properties of cold rolled and annealed materials G1, H1, H2, H3 and I2;

[0066] FIG. 5 shows the scanning electron micrographs of the molten zone after Nital etching and image analysis highlighting the effect of aluminum content on the cementite particles (in white) in the microstructure for the assemblies A+A, B+B, C+C and E+E as detailed in table 5;

[0067] FIG. 6 shows the heterogeneous weld strength characterized by cross-tensile specimen (A, B, C, E and F welded with J);

[0068] FIG. 7 illustrates the CTS coefficient as a function of Al content (A, B, C, E and F welded with J for heterogeneous);

[0069] FIG. 8 shows the welding range for homogeneous welding (A, B, C, E and F);

[0070] FIG. 9 shows the welding range for heterogeneous welding (A, B, C, E and F welded with J);

[0071] FIG. 10 shows the heterogeneous tensile shear stress results (A, B, C, E and F welded with J);

[0072] FIG. 11 shows the micrographs for spot welded joints with an aluminum alloyed steel containing 2.9 & 3.9% of Al (Spot welds E+E and F+F as detailed in table 5) and illustration of Martensite 18R;

[0073] FIG. 12 shows the micro-hardness filiations for homogeneous spot weld (A, B, C, E and F);

[0074] FIG. 13 shows the micro-hardness filiations for heterogeneous spot weld using an aluminum alloyed steel and a typical Dual Phase of 600 MPa of resistance. (A, B, C, E and F welded with J);

[0075] FIG. 14 illustrates the effect of the aluminum content in the molten zone on hardness (A, B, C, E and F welded with J for heterogeneous);

[0076] FIG. 15 shows the failure modes as a function of the Al content of an aluminum alloyed steel from 1 to 4% (left to right) for B, C, E and F;

[0077] FIG. 16A shows the heterogeneous plug ratios for examples A, B, C, E and F welded with J;

[0078] FIG. 16B shows the homogeneous plug ratios, for examples G and H;

[0079] FIG. 17 gives a schematic description of Tensile Shear and Cross-tension tests used to characterize the resistance of the spot weld;

[0080] FIG. 18 gives a non limitative example of a plug ratio and a molten zone geometry between an aluminum alloyed steel according to the invention and a Dual Phase 600 (DP). H is the MZ height, PD is the Plug diameter, MZ-D is MZ diameter, where MZ means Molten zone;

[0081] FIG. 19 shows the microprobe analysis images with a threshold at the nominal P content showing the effect of Al on the P segregation for A, B, C, E;

[0082] FIGS. 20A and B illustrate the surface fraction of areas with more than the nominal P content as the function of their size, FIG. 20A being for examples A, B, C, E while FIG. 20B is for G and H;

[0083] FIG. 21 shows the evolution of the surface fraction of areas larger than 20 μm.sup.2 with more than the nominal P content in the molten zone as a function of Al content for A, B, C, E; and

[0084] FIGS. 22A and B illustrate the CTS coefficient as a function of Al content with and without post treatment: A for examples A, B, C, E and F in homogeneous welding and B for examples A, B, C, E and F welded with J.

DETAILED DESCRIPTION

[0085] The present invention provides a spot welded joint of two steel sheets wherein at least one of the steel sheets, called an aluminum alloyed steel, presents yield strength above or equal to 600 MPa, an ultimate tensile strength above or equal to 1000 MPa, uniform elongation above or equal to 15%. The base metal chemical composition comprising more than 0.5% of Al, being easy to weld and to cold roll to its targeted final thickness. To do so, the chemical composition is very important as well as the annealing parameters so as to reach all the objectives. Following chemical composition elements are given in weight percent.

[0086] According to the invention, the carbon content is between 0.05 and 0.21%. Carbon is a gamma-former element. It promotes, with the invention Mn content, the stabilization of austenite. Below 0.05%, the tensile strength above 1000 MPa is difficult to achieve. If the carbon content is greater than 0.21%, the cold-rollability is reduced and the weldability becomes poor. Preferably, carbon content is between 0.10 and 0.21%.

[0087] Manganese must be between 4.0% and 7.0%. This element, also austenite-stabilizer, is used to stabilize enough austenite in the microstructure. It also has a solid solution hardening and a refining effect on the microstructure. For Mn content less than 4.0%, the retained austenite fraction in the microstructure is less than 20% and the combination of the uniform elongation above 15% and the tensile strength above 1000 is not achieved. Above 7.0%, weldability becomes poor, while segregations and inclusions deteriorate the damage properties.

[0088] With regard to aluminum, its content must be between 0.5% and 3.5%. Above 0.5 wt %, aluminum additions are interesting for many aspects to increase the stability of retained austenite through an increase of carbon in the retained austenite. Al enables to decrease the hardness of the hot band, which can be then easily cold rolled down to its final thickness as seen in FIGS. 1, 2 and 3. The robustness is also improved during annealing with Al additions. Addition of Al leads to lower variation of austenite fraction as a function of temperature and leads to improve plug ratio as illustrated in FIGS. 15 and 16. Furthermore, Al is the most efficient element when it comes to opening a large feasibility window for annealing temperature in continuous annealing since it favors the combination of advanced recrystallization at temperatures above the non-recrystallization temperature and austenite stabilization. Aluminum should be lower or equal to 3.5% to avoid the formation of coarse primary ferrite grains formed during the solidification and not transformed into austenite during further cooling, leading to tensile strength below 1000 MPa. It should be understood that since Al is alphageneous whilst C and Mn are both gammageneous, the optimum Al content to limit the formation of coarse primary ferrite grains decreases when C and Mn contents decrease.

[0089] Aluminum is also detrimental for continuous casting since the casting powder may react with the liquid metal, the kinetics of reaction being increased when Al content is increased. These coarse primary ferrite grains reduce the tensile strength below 1000 MPa. As a consequence, Al content is preferably between 1.0 and 3.0% and even more preferably between 1.0 and 2.5%.

[0090] Silicon is also very efficient to increase the strength through solid solution. However its content is limited to 2.0%, because beyond this value, the rolling loads increase too much and hot rolling process becomes difficult. The cold-rollability is also reduced. Preferably, to avoid edge cracks, Si content is lower than 1.5% or even lower than 1.0%.

[0091] Micro-alloying elements such as titanium, vanadium and niobium may be added respectively in an amount less than 0.2% for each, in order to obtain an additional precipitation hardening. In particular titanium and niobium are used to control the grain size during the solidification. One limitation, however, is necessary because beyond, a saturation effect is obtained.

[0092] As for sulphur, above a content of 0.004%, the ductility is reduced due to the presence of excess sulphides such as MnS, in particular hole-expansion tests show lower values in presence of such sulphides.

[0093] Phosphorus is an element which hardens in solid solution but which reduces the spot weldability and the hot ductility, particularly due to its tendency to segregation at the grain boundaries or co-segregation with manganese. For these reasons, its content must be limited to 0.025%, and preferably 0.020%, in order to obtain good spot weldability.

[0094] The maximum boron content allowed by the invention is 0.0035%. Above such limit, a saturation level is expected as regard to hardenability.

[0095] The balance is made of iron and inevitable impurities. Impurity level means below 0.04% of elements such as Ni, Cr, Cu, Mg, Ca . . . .

[0096] The steel microstructure contains, as surface fraction, 20% to 50% of austenite, 40% to 80% of annealed ferrite and martensite lower than 25%. The sum of these microstructural phases equals more than 95%. The balance is made of small inevitable precipitates such as carbides.

[0097] Austenite is a structure that brings ductility, its content must be above 20% so that the steel of the invention is enough ductile with uniform elongation above 15% and its content must be below 50% because above that value the mechanical properties balance deteriorates.

[0098] Ferrite in the invention is defined by a cubic center structure obtained from recovery and recrystallization upon annealing whether from preceding ferrite formed during solidification or from bainite or martensite of the hot rolled steel sheet. Hence, the term annealed ferrite implies that more than 70% of the ferrite is recrystallized. The recrystallized ferrite is characterized by a mean average misorientation, as measured by SEM-EBSD, lower than 3° inside the grains. Its content must be between 40 and 80% so as to have 1000 MPa minimum of tensile strength, with at least 600 MPa of yield strength and at least 15% of uniform elongation.

[0099] Martensite is the structure formed during cooling after the soaking from the unstable austenite formed during annealing. Its content must be limited to 25% so that the uniform elongation remains above 15%. A specific kind of martensite is the so-called 18R martensite structure which is an orthorhombic needle-like phase with a specific crystallography which has been identified and well documented by Cheng et al. [W.-C. Cheng, C.-F. liu, Y.-F. Lai, Scripta Mater., 48 (2003), pp. 295-300].

[0100] The method to produce the steel according to the invention implies casting steel with the chemical composition of the invention.

[0101] The cast steel is reheated between 1150° C. and 1300° C. When slab reheating temperature is below 1150° C., the rolling loads increase too much and hot rolling process becomes difficult. Above 1300° C., oxidation is very intense, which leads to scale loss and surface degradation.

[0102] Hot rolling the reheated slab is done at a temperature between 1250° C. and 800° C., the last hot rolling pass taking place at a temperature T.sub.lp above or equal to 800° C. If T.sub.lp is below 800° C., hot workability is reduced.

[0103] After hot rolling, the steel is cooled at a cooling speed V.sub.cooling1 between 1° C./s to 150° C./s, until the coiling temperature T.sub.coiling lower or equal to 650° C. Below 1° C./s, a coarse microstructure is formed and the final mechanical properties balance deteriorates. Above 150° C./s, the cooling process is difficult to control.

[0104] The coiling temperature T.sub.coiling must be lower or equal to 650° C. If the coiling temperature is above 650° C., coarse ferrite and bainite structure is formed leading to a more heterogeneous microstructure after cold-rolling and annealing.

[0105] Optionally, the steel undergoes an intermediate annealing at this stage to reduce its hardness and facilitate the subsequent cold-rolling process and eventually to avoid cracks during cold rolling. The annealing temperature shall be between 450° C. and 600° C. between 1 and 24 hours in the case of batch annealing, or between 650° C. and 750° C. between 20 and 180 s in the case of continuous annealing.

[0106] A further step includes descaling and cold rolling the steel with a cold rolling ratio between 30% and 70% so as to obtain a cold rolled steel with thickness generally between 0.6 and 3 mm. Below 30%, the recrystallization during subsequent annealing is not favored enough and the uniform elongation above 15% is not achieved due to a lack of recrystallization. Above 70%, there is a risk of edge cracking during cold-rolling.

[0107] Annealing can then be performed by heating the steel at a heating rate H.sub.rate at least equal to 1° C./s up to the annealing temperature T.sub.anneal. Such temperature T.sub.anneal has minimum and maximal values defined by the following equations:

T.sub.min=721−36*C−20*Mn+37*Al+2*Si, in ° C.

T.sub.max=690+145*C−6.7*Mn+46*Al+9*Si, in ° C.,

where the chemical composition elements are given in weight percent.

[0108] Controlling the annealing temperature is an important feature of the process since it enables to control the austenite fraction and its chemical composition as well as the recrystallization of the steel of the invention. Below T.sub.min, the minimum austenite fraction is not formed, or its stability is too high, leading to a limited tensile strength below 1000 MPa. Above T.sub.max, there is a risk to form too much martensite, leading to a limited uniform elongation below 15%.

[0109] After annealing, the steel sheet is cooled at a cooling rate between 5° C./s and 70° C./s.

[0110] Optionally, the steel sheet is cooled down to a temperature T.sub.OA between 350° C. and 550° C. and kept at T.sub.OA for a time between 10 and 300 seconds. It was shown that such a thermal treatment which facilitates the Zn coating by hot dip process for instance does not affect the final mechanical properties.

[0111] Optionally, the cold rolled and annealed steel sheet is tempered at a temperature T.sub.temper between 170 and 400° C. for a time t.sub.temper between 200 and 800 s. This treatment enables the tempering of martensite, which might be formed during cooling after the soaking from the unstable austenite. The martensite hardness is thus decreased and steel ductility is improved. Below 170° C., the tempering treatment is not efficient enough. Above 400° C., the strength loss becomes high and the balance between strength and ductility is not improved anymore.

[0112] The cold rolled and annealed steel sheet is afterwards spot welded so as to obtain a welded joint with high resistance.

[0113] To obtain a spot weld according to the invention, welding parameters can be defined as follows. Effective intensity can be between 3 kA and 15 kA. As a non limitative example, spot weld intensity according to the invention are shown in FIGS. 8 and 9. Force applied on the electrodes is between 150 and 850 daN. Electrode active face diameter is between 4 and 10 mm. A suitable spot weld is defined by its molten zone characteristic dimension. Its molten zone height is between 0.5 and 6 mm and diameter between 3 and 12 mm as in FIG. 18.

[0114] The spot welded joint according to the invention is characterized by a molten zone microstructure containing a surface fraction of coarse segregated areas lower than 1%. The coarse segregated areas are defined as zones larger than 20 μm.sup.2 containing phosphorus in an amount superior to the base metal nominal phosphorus content. Above such value, the segregation is too high, which decreases the nugget toughness as in FIGS. 19, 20 and 21.

[0115] In addition, the molten zone microstructure contains a density of iron carbides larger than 50 nm equal or above 2×10.sup.6 per mm.sup.2. Below such density, martensite is not enough tempered and the nugget microstructure does not present enough toughness as in FIGS. 5, 12, 13 and 14.

[0116] Preferably, in at least one side of the welded joint, the microstructure at the boundary between molten zone and the steel according to the invention does not have any martensite 18R inside the ferritic grains so that the coarse grain zone keeps enough toughness as in FIG. 11 for the 3% Al content.

[0117] Optionally, the spot welded joint according to the invention undergoes a thermal post treatment to further improve the spot weld resistance as illustrated in FIGS. 22A and B. Such post treatment can be done both on homogeneous or heterogeneous welding. The oven post treatment consists in an austenitization treatment over 1000° C. for at least 3 minutes followed by a rapid cooling i.e above 50° C./s for the welded joint.

[0118] The in situ post treatment consists, after welding in a two step treatment:

[0119] A first step without any applied current of at least 0.2 seconds

[0120] A second step consisting in applying to the welded joint a current between 60% and 90% of the mean intensity applied during welding.

[0121] so as to temper the martensite and improve the toughness of the nugget and the Heat Affected Zone. The total time of the step 1 and step 2 is between 0.1 to 2 seconds.

[0122] The invention will be better understood with the following non limitative examples. Indeed, the spot welded steel of the invention can be obtained with any other steel as, for instance: Interstitial free steels, Dual phase steels, TRIP steels, BH steels, Press hardened steels, multiphase steels.

[0123] Semi-finished products have been produced from a steel casting. The chemical compositions of the semi-finished products, expressed in weight percent, are shown in Table 1 below. The rest of the steel composition in Table 1 consists of iron and inevitable impurities resulting from the smelting.

TABLE-US-00001 TABLE 1 Chemical composition (wt %). C Mn Al Si P S Nb A 0.209 4.91 0.024 0.013 0.02 0.001 B 0.196 5.01 1.03 0.012 0.022 0.002 C 0.192 5.03 1.87 0.014 0.021 0.002 D 0.188 4.9 1.9 0.017 0.02 0.002 E 0.189 5.01 2.85 0.02 0.02 0.0021 F 0.175 4.77 3.72 0.024 0.02 0.0023 G 0.109 5.28 0.02 0.52 0.018 0.0034 H 0.109 5.17 1.81 0.507 0.017 0.0035 I 0.123 5.05 1.71 0.521 0.008 0.004 0.032 J 0.089 1.82 0.01 0.145 0.015 0.003

[0124] Ti and V contents of steels A to J are lower than 0.010%. Boron content is lower than 35 ppm.

[0125] The steels A to I have first been reheated and hot-rolled down to 2.4 mm thick plates. Steel J is a typical Dual Phase steel with 600 MPa of tensile strength, such type of steel is known by the man skilled in the art, it is used as the steel to which steels A to I are welded to for heterogeneous welding cases. The hot rolled steel plates A to I were then cold rolled and annealed. The process parameters undergone are shown in Table 2 with the following abbreviations:

[0126] T.sub.reheat: is the reheating temperature;

[0127] T.sub.lp: is the finishing rolling temperature;

[0128] V.sub.cooling1: cooling rate after last hot rolling pass;

[0129] T.sub.coiling: is the coiling temperature;

[0130] IA T: is the temperature of the intermediate annealing performed on the hot band;

[0131] IA t: is the duration of the intermediate annealing performed on the hot band;

[0132] Rate: is the rate of cold rolling reduction;

[0133] H.sub.rate: is the heating rate;

[0134] T.sub.anneal: is the soaking temperature during annealing;

[0135] t.sub.anneal: is the soaking duration during annealing; and

[0136] V.sub.cooling2: is the cooling rate after annealing to room temperature.

TABLE-US-00002 TABLE 2 Hot-rolling and cold-rolling and annealing conditions. T.sub.reheat T.sub.lp V.sub.cooling1 T.sub.coiling IA T IA t Rate H.sub.rate T.sub.anneal t.sub.anneal Vcooling2 (° C.) (° C.) (° C./s) (° C.) (° C.) (min) (%) (° C./s) T.sub.min T.sub.max (° C.) (s) (° C./s) A1 1250 950 8 650 70 10 616 689 700 60 10 B1 1250 940 8 600 50 10 652 732 710 120 8 C1 1250 940 8 600 50 10 683 770 720 120 8 D1 1250 900 8 650 50 10 687 772 710 150 5 D2 1250 900 8 650 50 10 687 772 720 150 5 D3 1250 900 8 650 50 10 687 772 730 150 5 D4 1250 900 8 20 50 10 687 772 710 150 5 D5 1250 900 8 20 50 10 687 772 720 150 5 D6 1250 900 8 20 50 10 687 772 730 150 5 D7 1250 900 8 550 50 10 687 772 710 150 5 D8 1250 900 8 550 50 10 687 772 720 150 5 D9 1250 900 8 550 50 10 687 772 730 150 5 D10 1250 900 8 550 700 2 50 10 687 772 710 150 5 D11 1250 900 8 550 700 2 50 10 687 772 720 150 5 D12 1250 900 8 550 700 2 50 10 687 772 730 150 5 D13 1250 900 8 550 700 2 50 10 687 772 740 150 5 D14 1250 900 8 550 500 300 50 10 687 772 710 150 5 D15 1250 900 8 550 500 300 50 10 687 772 720 150 5 D16 1250 900 8 550 600 300 50 10 687 772 720 150 5 D17 1250 900 8 550 600 300 50 10 687 772 730 150 5 D18 1250 900 8 550 70 10 687 772 710 150 5 D19 1250 900 8 550 70 10 687 772 720 150 5 D20 1250 900 8 550 70 10 687 772 730 150 5 E1 1250 940 8 600 50 10 719 815 770 120 8 F1 1250 900 65 450 50 10 757 855 810 120 8 G1 1250 900 8 600 600 300 50 10 613 676 690 150 8 H1 1250 900 8 600 600 300 50 10 682 759 740 150 8 H2 1250 900 8 600 600 300 50 10 682 759 770 150 8 H3 1250 900 8 600 700 2 50 10 682 759 740 150 8 I1 1250 900 8 600 600 300 50  20* 680 757 730 150 8 I2 1250 900 8 600 600 300 50  20* 680 757 740 150 8 I3 1250 900 8 600 600 300 50  20* 680 757 750 150 8

[0137] In table 2, “blank” means that no intermediate annealing was performed and “*” means that the heating rate was 20° C./s up to 600° C. and then 1° C./s up to the annealing temperature.

[0138] The table 3 presents the following characteristics:

[0139] Ferrite: “OK” refers to the presence of ferrite with a volume fraction between 40 and 80% in the microstructure of the annealed sheet. “KO” refers to comparative examples where ferrite fraction is outside this range.

[0140] Austenite: “OK” refers to the presence of austenite with a volume fraction between 20 and 50% in the microstructure of the annealed sheet. “KO” refers to comparative examples where austenite fraction is outside this range.

[0141] Martensite: “OK” refers to the presence or not of martensite with a volume fraction less than 25% in the microstructure of the annealed sheet. “KO” refers to comparative examples where martensite fraction is above 25%.

[0142] UTS (MPa) refers to the ultimate tensile strength measured by tensile test in the longitudinal direction relative to the rolling direction.

[0143] YS (MPa) refers to the yield strength measured by tensile test in the longitudinal direction relative to the rolling direction.

[0144] UEI (%) refers to the uniform elongation measured by tensile test in the longitudinal direction relative to the rolling direction.

[0145] YS/TS refers to the ratio between Yield strength and ultimate tensile strength.

[0146] TEI refers to the total elongation measured on ISO 12.5×50 specimen.

TABLE-US-00003 TABLE 3 Properties of cold-rolled and annealed sheets Ferrite Austenite martensite YS(MPa) TS (MPa) UEI (%) YS/TS EI TS*EI A1 OK (48%) OK (26%) KO (26%) 499 1250 14 0.4 15.4 19250 B1 OK (55%) OK (45%) OK (5%) 860 1075 23 0.8 25.9 27896 C1 OK (60%) OK (40%) OK (0%) 812 1023 24 0.79 27.0 27621 D1 OK OK OK 872 1082 26 0.81 30.7 33253 D2 OK OK OK 824 1171 21 0.7 24.2 28338 D3 OK OK OK 758 1239 17 0.61 20.5 25338 D4 OK OK OK 865 1018 27 0.85 33.3 33865 D5 OK OK OK 837 1150 21 0.73 24.9 28673 D6 OK OK OK 792 1228 18 0.64 21.2 26075 D7 OK OK OK 882 1101 28 0.8 33.0 36333 D8 OK OK OK 817 1187 19 0.69 22.4 26589 D9 OK OK OK 769 1252 17 0.61 20.0 24998 D10 OK OK OK 883 1033 27 0.85 33.6 34743 D11 OK OK OK 872 1085 29 0.8 34.8 37722 D12 OK OK OK 806 1154 24 0.7 29.8 34351 D13 OK OK OK 774 1217 21 0.64 24.6 29979 D14 OK OK OK 810 1056 27 0.77 31.8 33546 D15 OK OK OK 683 1224 16 0.56 18.6 22766 D16 OK OK OK 787 988 26 0.8 30.1 29706 D17 OK OK OK 755 1078 22 0.7 26.1 28100 D18 OK OK OK 718 1146 18 0.63 21.6 24792 D19 OK OK OK 904 1098 28 0.82 30.9 33965 D20 OK OK OK 880 1154 24 0.76 27.8 32081 D21 OK OK OK 796 1252 17 0.64 18.7 23412 E1 OK (61%) OK (37%) OK (2%) 698 1007 23 0.69 26.7 26887 F1 OK (35%) OK (65%) OK (0%) 560 840 26 0.67 29.4 24696 G1 OK (52%) KO (17%) KO (31%) 701 1060 13 0.66 14.4 15264 H1 OK (68%) OK (27%) OK (5%) 624.5 1002 17 0.62 19.7 19689 H2 OK (57%) KO (15%) KO (28%) 516 1138 9 0.45 10.3 11665 H3 OK OK OK 690.5 1006.5 18 0.69 21.1 21237 I1 OK OK OK 875 1026.5 18 0.85 20.6 21146 I2 OK OK OK 845.5 1063 17 0.80 20.0 21207 I3 OK OK OK 804.5 1082 16 0.74 18.6 20071

[0147] The steels A to I are then spot welded to a DP 600 GI as an example following the welding parameters presented in table 4: Sheet thickness for A to I material and DP600 GI is 1.2 mm. The welding parameters are the same between grades and differ only between homogeneous and heterogeneous welding.

TABLE-US-00004 TABLE 4 steel welding parameters. Electrod Current Squeezing Welding Holding active face Electrode frequency time time time diameter Force (Hz) (period) (period) (period) (mm) (daN) Homogeneous 50 70 14 14 6 400 Heterogeneous 50 70 15 15 6 400

[0148] The different values are explained here below:

[0149] Welding current range: The welding current (also called welding intensity) range is expressed in kA. The minimum of the weld range is defined by the welding current necessary to develop a nugget that diameter is 4.25√t or more, where t is the thickness of the material in mm. The maximum of the welding current range is defined by the current at which expulsion of the molten metal from the nugget occurs.

[0150] Alpha value is the maximum load in cross test divided by the weld diameter and the thickness. It is a normalised load for resistant spot welding expressed in daN/mm.sup.2.

[0151] Plug ratio: The plug ratio is equal to the plug diameter divided by the MZ diameter. The lower the plug ratio, the lower the molten zone toughness as shown in FIG. 18.

TABLE-US-00005 TABLE 5 spot welded results. CGHAZ means coarse grain heat affected zone. number density of Surface Average Presence of carbides fraction of nugget ferrite at larger than coarse TSS average hardness Nugget MZ/CGHAZ 50 nm in the segregated Welding Alpha CTS strength Assembly (Hv) microstructure boundary nugget (mm.sup.−2) area (%) range (kA) (daN/mm.sup.2) (daN) A1 + A1 535 Martensite No 0.72 × 10.sup.6 1.32 2 21 790 B1 + B1 505 Martensite No 3.12 × 10.sup.6 0.26 2.5 28 1644 D1 + D1 480 Martensite No 8.66 × 10.sup.6 0.083 2.5 38 1590 E1 + E1 422 Bainite + delta YES 9.55 × 10.sup.6 0.041 1.8 52 1800 ferrite F1 + F1 308 Martensite + delta YES Not Not 2 29 1213 ferrite measured measured A1 + J1 487 Martensite No Not Not 2.8 26 813 measured measured B1 + J1 443 Martensite No Not Not 2.3 37 951 measured measured D1 + J1 456 Martensite No Not Not 2 39 1004 measured measured E1 + J1 464 Martensite YES Not Not 1.9 53 1070 measured measured F1 + J1 405 Martensite YES Not Not 2 30 697 measured measured G1 + G1 502 Martensite NO Not 2.83 2.4 31 1439 measured H1 + H1 451 Martensite NO 6.17 × 10.sup.6 0.22 1.6 77 1599 I1 + I1 Not Martensite NO Not Not Not 85 Not measured measured measured measured measured G1 + J1 Not Martensite NO Not Not 3 52 1522 measured measured measured H1 + J1 Not Martensite NO Not Not 1.6 90 1407 measured measured measured

[0152] All cold rolled and annealed steels produced with chemical compositions from B, C, D, E, H (excepted H2) and I are produced according to the invention, they present YS above 600 MPa, tensile strength above 1000 MPa and uniform elongation 15% as illustrated in FIG. 4A for B1, C1, E1 and F1 (reference) and FIG. 4B for G1, H1, H2, H3, and I2 where G1 and H2 are references. The chemical composition is within the targeted range as well as the microstructure; the process parameters of the invention have also been followed. A1, F1, G1, and H2 are not according to the invention. Resistance testing of spot welds has been done according to test as depicted in FIG. 17. They are called tensile shear tests and cross tension tests. These tests are used to determine the weld strength. As shown in FIGS. 6, 7 and 10, the spot weld resistance increases with Al content within the Al range of the invention.

[0153] Furthermore an examination of macro-etch specimens can reveal the nugget diameters (FIG. 11) as well as penetration and weld microstructures in the different zones.

[0154] When it comes to the thermal post treatments, as can be seen from FIG. 22, Cross Tensile Strength coefficient is further improved with this said treatment for spot welded joints with at least one Al containing steel. This is due to the alphageneous effect of Al which opens a tempering window below Ac1 allowing not to re-austenitize upon welding the critical parts of the welded joint.

[0155] The steel sheets assembly according to the invention will be beneficially used for the manufacture of structural or safety parts in the automobile industry.