PROJECTION WELDED JOINT AND PROJECTION WELDING METHOD

Abstract

A projection welded joint is formed by joining a steel sheet having a tensile strength of 980 MPa or higher and a nut by performing projection welding. In a hardness distribution from the steel sheet to the nut through a weld metal zone, and a hardened region exists on each of the steel sheet side and the nut side. A hardness of each hardened region is higher than that of the base metal on the corresponding side, and each hardened region extends continuously for a distance of 500 .Math.m or more. The maximum hardness .sub.NHmax on the nut side is higher than the maximum hardness .sub.SHmax on the steel sheet side. A region where the maximum hardness .sub.SHmax on the steel sheet side exists is formed of a martensite microstructure having a prior austenite grain size of 20 .Math.m or less.

Claims

1. A projection welded joint comprising: a steel sheet joined to a nut by projection welding at a weld metal zone at a joint interface between the steel sheet and the nut, wherein: a hardness distribution in a cross section of the projection welded joint extending from the steel sheet to the nut through the weld metal zone includes: a first hardened region which exists on a side of the steel sheet with respect to a center of the weld metal zone and which extends continuously for a distance of 500 .Math.m or more, the first hardened region having: a hardness .sub.sH1 that is higher than a hardness .sub.sH0 of a base metal of the steel sheet, and a maximum hardness .sub.SHmax; and a second hardened region which exists on a side of the nut with respect to the center of the weld metal zone and which extends continuously for a distance of 500 .Math.m or more, the second hardened region having: a hardness .sub.NH1 that is higher than a hardness .sub.NH0 of a base metal of the nut, and a maximum hardness .sub.NHmax that is higher than the maximum hardness .sub.SHmax on the side of the steel sheet; a region of the projection welded joint which has a center located at a position corresponding to the maximum hardness .sub.SHmax and which extends for a distance of 500 .Math.m in a direction parallel to the joint interface and a distance of 50 .Math.m in a direction perpendicular to the joint interface is formed of a martensite microstructure having a prior austenite grain size of 20 .Math.m or less, and the steel sheet has a tensile strength of 980 MPa or higher and a chemical composition comprising, by mass %: C: 0.08% or more and 0.20% or less, Si: 0.2% or more and 1.6% or less, Mn: 1.0% or more and 3.4% or less, P: 0.05% or less, S: 0.01% or less, Al: 0.01% or more and 0.10% or less, N: 0.01% or less, one or more selected from: Nb: 0.005% or more and 0.050% or less, and Ti: 0.005% or more and 0.050% or less, and Fe and incidental impurities.

2. The projection welded joint according to claim 1, wherein: the hardness .sub.SH1 on the side of the steel sheet satisfies relational expression (1) below: $\begin{array}{cc}{}_{\text{s}}\text{H1}\ge 1.1{\times }_{\text{S}}\text{H0}& \text{­­­(1)}\end{array}$ the hardness .sub.NH1 on the side of the nut satisfies relational expression (2) below: $\begin{array}{cc}{}_{\text{N}}\text{H1}\ge \text{1}\text{.1}\times {}_{\text{N}}\text{H0}& \text{­­­(2)}\end{array}$ .

3. The projection welded joint according to claim 1, wherein the maximum hardness .sub.NHmax on the side of the nut and the maximum hardness .sub.SHmax on the side of the steel sheet satisfy relational expression (3) below: $\begin{array}{cc}{}_{\text{N}}\text{Hmax}\ge \text{1}\text{.02}{\times }_{\text{S}}\text{Hmax}& \text{­­­(3)}\end{array}$ .

4. The projection welded joint according to claim 1, wherein the chemical composition further comprises, by mass%, one or more selected from: B: 0.0050% or less, V: 0.05% or less, Cr: 0.50% or less, Mo: 0.50% or less, Co: 0.50% or less, Cu: 0.50% or less, Ni: 0.50% or less, Sb: 0.020% or less, and Ca and/or REM: 0.0050% or less.

5. The projection welded joint according to claim 1, wherein the steel sheet has a zinc-based coating layer.

6. A projection welding method comprising: joining the steel sheet and the nut according to claim 1 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75\right)& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 1.

7. The projection welded joint according to claim 2, wherein the maximum hardness .sub.NHmax on the side of the nut and the maximum hardness .sub.SHmax on the side of the steel sheet satisfy relational expression (3) below: .sub.NHmax ≥ 1.02 × .sub.SHmax (3).

8. The projection welded joint according to claim 2, wherein the chemical composition further comprises, by mass%, one or more selected from: B: 0.0050% or less, V: 0.05% or less, Cr: 0.50% or less, Mo: 0.50% or less, Co: 0.50% or less, Cu: 0.50% or less, Ni: 0.50% or less, Sb: 0.020% or less, and Ca and/or REM: 0.0050% or less.

9. The projection welded joint according to claim 2, wherein the steel sheet has a zinc-based coating layer.

10. The projection welded joint according to claim 4, wherein the steel sheet has a zinc-based coating layer.

11. The projection welded joint according to claim 8, wherein the steel sheet has a zinc-based coating layer.

12. A projection welding method comprising: joining the steel sheet and the nut according to claim 2 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 2.

13. A projection welding method comprising: joining the steel sheet and the nut according to claim 3 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 3.

14. A projection welding method comprising: joining the steel sheet and the nut according to claim 4 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 4.

15. A projection welding method comprising: joining the steel sheet and the nut according to claim 5 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 5.

16. A projection welding method comprising: joining the steel sheet and the nut according to claim 7 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 7.

17. A projection welding method comprising: joining the steel sheet and the nut according to claim 8 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 8.

18. A projection welding method comprising: joining the steel sheet and the nut according to claim 9 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 9.

19. A projection welding method comprising: joining the steel sheet and the nut according to claim 10 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.25\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 10.

20. A projection welding method comprising: joining the steel sheet and the nut according to claim 11 by projection welding under the following conditions: the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes, and the tensile strength M (MPa) of the steel sheet and energizing time T (s) of the projection welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below: $\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$ thereby producing the projection welded joint according to claim 11.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0031] FIG. 1(a) to FIG. 1(c) are schematic diagrams illustrating the cross section and hardness distribution of a projection welded joint in an example of an embodiment (in the case of a weld metal zone having a lump shape).

[0032] FIG. 2(a) to FIG. 2(c) are schematic diagrams illustrating the cross section and hardness distribution of a projection welded joint in another example of an embodiment that differs from the one illustrated in FIG. 1(a) to FIG. 1(c) (in the case of a weld metal zone having a film shape).

[0033] FIG. 3 is a schematic diagram illustrating comparative example A in which the hardness distribution of a projection welded joint is beyond the range of the disclosed embodiments.

[0034] FIG. 4 is a schematic diagram illustrating comparative example B in which the hardness distribution of a projection welded joint is beyond the range of the disclosed embodiments.

[0035] FIG. 5 is a schematic diagram illustrating comparative example C in which the hardness distribution of a projection welded joint is beyond the range of the disclosed embodiments.

[0036] FIG. 6 is a diagram illustrating the actual measurement data of the hardness distribution of sample No. 3 (example of the disclosed embodiments) in EXAMPLES of the disclosed embodiments.

[0037] FIG. 7 is a diagram illustrating the actual measurement data of the hardness distribution of sample No. 4 ((example of the disclosed embodiments) in EXAMPLES of the disclosed embodiments.

[0038] FIG. 8 is a diagram illustrating the actual measurement data of the hardness distribution of sample No. 7 (comparative example) in EXAMPLES of the disclosed embodiments.

[0039] FIG. 9 is a diagram illustrating the actual measurement data of the hardness distribution of sample No. 10 (comparative example) in EXAMPLES of the disclosed embodiments.

[0040] FIG. 10 is a diagram illustrating the actual measurement data of the hardness distribution of sample No. 11 (comparative example) in EXAMPLES of the disclosed embodiments.

[0041] FIG. 11 is a diagram illustrating the range of the welding condition E in the range of the disclosed embodiments (E: 0.20 to 0.75) in a graph illustrating the relationship between the welding condition E and peeling strength FS in EXAMPLES of the disclosed embodiments.

[0042] FIG. 12 is a schematic diagram illustrating the nut for welding used in EXAMPLES of the disclosed embodiments, where FIG. 12(a) illustrates a back view of the nut, FIG. 12(b) and FIG. 12(c) illustrate side views of the nut, and FIG. 12(d) illustrates a partially enlarged view of the projection part of the nut.

DETAILED DESCRIPTION

[0043] The disclosed embodiments include a welded joint formed by joining a steel sheet (high strength steel sheet) having a tensile strength of 980 MPa or higher and a nut by performing projection welding. Hereafter, an embodiment of the disclosed embodiments will be described with reference to the figures.

[0044] FIGS. 1(a) to 1(c) are schematic diagrams illustrating, in the case of a weld metal zone 4 having a lump shape in the embodiment, the cross section and an example of hardness distribution of a projection welded joint 10, and the front view of the welded joint. FIGS. 2(a) to 2(c) are schematic diagrams illustrating, in the case of a weld metal zone 4 having a film shape in the embodiment, the cross section and an example of hardness distribution of a projection welded joint 10, and the front view of the welded joint.

[0045] FIG. 1(a) and FIG. 2(a) are the enlarged cross-sectional views of the joined states of a nut 1 and a steel sheet 2, which are illustrated in the below-described FIG. 1(c) and FIG. 2(c), respectively (FIG. 1(a) is the enlarged view of portion A in FIG. 1(c), and FIG. 2(a) is the enlarged view of portion B in FIG. 2(c)), and hardness distribution graphs. FIG. 1(b) and FIG. 2(b) are front views illustrating the states before welding is performed to provide the states illustrated by the below-described FIG. 1(c) and FIG. 2(c), respectively. FIG. 1(c) and FIG. 2(c) are cross-sectional diagrams illustrating the joined states of a whole nut 1 and a steel sheet 2. Here, in these examples, the nut 1 before welding is performed has three projection parts 3 (protruding parts compressed to the steel sheet when welding is performed).

[0046] As in the case of such examples, in the disclosed embodiments, it is necessary that, in the hardness distribution from the steel sheet 2 to the nut 1 through the weld metal zone 4, each of a hardened region which exists on the steel sheet 2 side with respect to the center of the weld metal zone 4 and whose hardness .sub.sH1 is higher than the hardness .sub.sH0 of the base metal of the steel sheet (that is, .sub.sH1 > .sub.sH0) and a hardened region which exists on the nut 1 side with respect to the center of the weld metal zone 4 and whose hardness .sub.NH1 is higher than the hardness .sub.NH0 of the nut base metal (that is, .sub.NH1 > .sub.NH0) extend continuously for a distance of 500 .Math.m or more.

[0047] This is because, in the case where the continuously existing range of the hardened region on at least one of the steel sheet 2 side and the nut 1 side is less than 500 .Math.m, it is not possible to achieve a satisfactory joined state at the interface between the steel sheet 2 and the nut 1 due to insufficient heat input, which results in insufficient peeling strength. Therefore, the continuously existing range of the hardened region described above is set to be 500 .Math.m or more or preferably 600 .Math.m or more. There is no particular limitation on the upper limit of the continuously existing range of the hardened region described above. It is preferable that the continuously existing range of the hardened region described above be 2000 .Math.m or less or more preferably 1500 .Math.m or less from the viewpoint of preventing burrs from occurring and deformation from occurring in the nut due to excessive heat input.

[0048] Here, in the disclosed embodiments, a case of a peeling strength FS, which is measured by using the method described in EXAMPLES below, of 9.0 kN or higher is a case of excellent peeling strength.

[0049] Incidentally, the hardness is represented by Vickers hardness HV, and it is preferable that the hardness be measured under the measuring conditions of a testing force of 0.9807 N to 2.942 N and a measuring interval of 50 .Math.m to 200 .Math.m. Here, in the disclosed embodiments, it is possible to measure the hardness by using the method described in EXAMPLES below.

[0050] Moreover, in the disclosed embodiments, in the two hardened regions described above, it is necessary that the maximum hardness .sub.NHmax on the nut 1 side be higher than the maximum hardness .sub.sHmax on the steel sheet 2 side (that is, .sub.sHmax > .sub.sHmax).

[0051] This is because, even if the continuously existing ranges of the hardened regions on the steel sheet 2 side and on the nut 1 side are both 500 .Math.m or more, in the case where .sub.NHmax is equal to or lower than .sub.sHmax, since a microstructure in the weld heat affected zone on the nut side fractures, the hardness of the microstructure on the nut side becomes the controlling factor of peeling strength, which results in insufficient peeling strength due to peeling strength being equal to or lower than the property of the high strength steel sheet. Therefore, the maximum hardness in the hardened region on the nut 1 side and the maximum hardness in the hardened region on the steel sheet 2 side should satisfy the relational expression .sub.NHmax > .sub.sHmax or preferably .sub.NHmax > 1.02 × .sub.sHmax. Here, it is preferable that the maximum hardness .sub.NHmax on the nut 1 side satisfy the relational expression 2.0 × .sub.sHmax ≥ .sub.NHmax from the viewpoint of preventing a deterioration in the toughness of the microstructure on the nut side.

[0052] Incidentally, the expression “maximum hardness” denotes the maximum hardness of a weld heat affected zone (HAZ). The HAZ (not illustrated) exists as a continuous region adjacent to the weld metal zone 4 (synonymous with nugget). The existing range of the HAZ includes the hardened region described above excluding the weld metal zone 4 described above, or, in the case where the HAZ does not include a softened region (region whose hardness is lower than that of the base metal), the existing range of the HAZ is identical to the hardened region described above excluding the weld metal zone 4 described above.

[0053] Moreover, in the disclosed embodiments, it is necessary that a region 5 (which is also briefly referred to as “region where .sub.sHmax exists” hereinafter) which has the center thereof at the position corresponding to the maximum hardness .sub.sHmax on the steel sheet 2 side and which extends for a distance of 500 .Math.m in a direction parallel to a joint interface (that is, parallel to the surface of the steel sheet 2) and a distance of 50 .Math.m in a direction perpendicular to the joint interface (that is, parallel to the thickness direction of the steel sheet 2) be formed of a martensite microstructure having a prior austenite grain size of 20 .Math.m or less.

[0054] In the examples illustrated in FIG. 1(a) and FIG. 2(a), the expression “region 5 where .sub.sHmax exists” denotes the hatched square region in each of the figures. That is, the expression “region 5 where .sub.sHmax exists” denotes, when a rectangle having sides having respective lengths of 50 .Math.m and 500 .Math.m is arranged so that a side having a length of 50 .Math.m is parallel to the thickness direction of the steel sheet 2 and a side having a length of 500 .Math.m is parallel to the surface of the steel sheet 2 and so that the hardness measuring point corresponding to the maximum hardness .sub.sHmax is identical to the intersection of the diagonal lines of such a rectangle, a region surrounded by such a rectangle.

[0055] Even if the continuously existing ranges of the hardened regions on the steel sheet 2 side and on the nut 1 side are both 500 .Math.m or more, and even if the relational expression .sub.NHmax > .sub.sHmax is satisfied, in the case where the region 5 where .sub.sHmax exists is formed of a microstructure (for example, bainite microstructure) which is different from a martensite microstructure, there is a decrease in hardness compared with the case of a martensite microstructure, which results in insufficient peeling strength.

[0056] Even if the continuously existing ranges of the hardened regions on the steel sheet 2 side and on the nut 1 side are both 500 .Math.m or more, even if the relational expression .sub.NHmax > .sub.sHmax is satisfied, and even if the region 5 where .sub.sHmax exists is formed of a martensite microstructure, in the case where a prior austenite grain size in the region 5 where .sub.sHmax exists is more than 20 .Math.m, there is an increase in hydrogen sensitivity, which results in a deterioration in delayed fracture resistance. Here, it is preferable that the prior austenite grain size in the region 5 where .sub.sHmax exists be 15 .Math.m or less and 1 .Math.m or more from the viewpoint of improving delayed fracture resistance and of the possibility of microstructure formation in the projection welding process of a nut.

[0057] That is, according to the disclosed embodiments, by forming a projection welded joint between a high strength steel sheet and a nut, in which the continuously existing ranges of the hardened regions on the steel sheet side and on the nut side are both 500 .Math.m or more, in which the relational expression .sub.NHmax > .sub.sHmax is satisfied, and in which a region 5 where .sub.sHmax exists is formed of a martensite microstructure having a prior austenite grain size of 20 .Math.m or less, it is possible to improve peeling strength while achieving satisfactory delayed fracture resistance.

[0058] Incidentally, by decreasing welding heat input, the nut 1 and the steel sheet 2 are joined through a film-shaped weld metal zone 4 as illustrated in FIG. 2(a) to FIG. 2(c). Even in this case, according to the disclosed embodiments, it is possible to improve peeling strength while achieving satisfactory delayed fracture resistance.

[0059] Here, the disclosed embodiments may further have the features described below in addition to the features described above.

[0060] From the viewpoint of further improving peeling strength, it is preferable that, when the hardness of the base metal of the steel sheet is defined as .sub.sH0, the hardness .sub.sH1 on the steel sheet 2 side satisfy relational expression (1) below and that, when the hardness of the nut base metal is defined as .sub.NH0, the hardness .sub.NH1 on the nut 1 side satisfy relational expression (2) below. This is because, as a result of these relational expressions being satisfied, it is possible to identify the hardened regions due to the effect of a variation in the measured values of the base metal hardness being eliminated. It is more preferable that the relational expression .sub.sH1 ≥ 1.2 × .sub.sH0, in which the lower limit of the relational expression (1) is modified, be satisfied and that the relational expression .sub.NH1 ≥ 1.2 × .sub.NH0, in which the lower limit of the relational expression (2) is modified, be satisfied.

[00005]$\begin{array}{cc}{}_{\text{S}}\text{H}1\ge 1.1\times {}_{\text{S}}\text{H}0& \text{­­­(1)}\end{array}$

[00006]$\begin{array}{cc}{}_{\text{N}}\text{H}1\ge 1.1\times {}_{\text{N}}\text{H}0& \text{­­­(2)}\end{array}$

[0061] Here, from the viewpoint of achieving satisfactory toughness of a microstructure formed in the weld, it is preferable that the relational expression 2.0 × .sub.sH0 ≥ .sub.sH1, in which the upper limit of the relational expression (1) is set, be satisfied. For the similar reason, it is preferable that the relational expression 2.0 × .sub.NH0 ≥ .sub.NH1, in which the upper limit of the relational expression (2) is set, be satisfied.

[0062] In addition, similarly, from the viewpoint of further improving peeling strength, it is preferable that the maximum hardness .sub.NHmax in the weld heat affected zone on the nut 1 side and the maximum hardness .sub.sHmax in the weld heat affected zone on the steel sheet 2 side satisfy relational expression (3) below. This is because, as a result of this relational expression being satisfied, since the weld heat affected zone is broken on the high strength steel sheet side, high peeling strength is achieved due to the high strength property of the high strength steel sheet.

[00007]$\begin{array}{cc}{}_{\text{N}}\text{Hmax}\ge 1.02\times {}_{\text{S}}\text{Hmax}& \text{­­­(3)}\end{array}$

[0063] Here, from the viewpoint of achieving satisfactory toughness of a microstructure formed in the weld, it is preferable that the relational expression 2.0 × .sub.sHmax ≥ .sub.NHmax, in which the upper limit of the relational expression (3) is set, be satisfied.

[0064] On the other hand, FIG. 3, FIG. 4, and FIG. 5 are schematic diagrams illustrating comparative examples A, B, and C, respectively, in which the hardness distribution in the case of a weld metal zone 4 having a film shape or a lump shape is beyond the range of the disclosed embodiments. In the case of comparative example A and comparative example B, the maximum hardness .sub.NHmax on the nut 1 side is higher than the maximum hardness .sub.sHmax on the steel sheet 2 side. However, since the continuously existing range of the hardened region on the nut 1 side is less than 500 .Math.m in the case of comparative example A (FIG. 3), and since the continuously existing range of the hardened region on the steel sheet 2 side is less than 500 .Math.m in the case of comparative example B (FIG. 4), there is insufficient peeling strength in both cases, which makes it impossible to solve the problems described above. On the other hand, in the case of comparative example C (FIG. 5), the continuously existing range of each of the hardened regions on the nut 1 side and on the steel sheet 2 side is 500 .Math.m or more. However, since the maximum hardness .sub.NHmax on the nut 1 side is equal to or lower than the maximum hardness .sub.sHmax on the steel sheet 2 side (.sub.NHmax ≤ .sub.sHmax), there is insufficient peeling strength, which makes it impossible to solve the problems described above.

[0065] Incidentally, it is preferable that the thickness of the steel sheet 2 used in the disclosed embodiments be within the thickness range of a steel sheet having a high demand as an automobile steel sheet. Examples of such a thickness range include a range of 0.4 mm to 3.2 mm.

[0066] Hereafter, the chemical composition of the steel sheet 2 used in the disclosed embodiments will be described.

[0067] This chemical composition is not only preferable as the chemical composition of a high strength cold rolled steel sheet having a TS of 980 MPa class or above but also necessary for, regarding a projection welded joint, improving the peeling strength while achieving delayed fracture resistance. Hereafter, “%” used when describing a chemical composition denotes “mass%”.

C: 0.08% or More and 0.20% or Less

[0068] C is an element which is effective for increasing the strength of a steel sheet. Moreover, C is an element which forms Ti- or Nb-based precipitates, which are important in the disclosed embodiments. However, in the case where the C content is less than 0.08%, it is difficult to achieve satisfactory strength of a steel sheet. Therefore, the C content is set to be 0.08% or more. It is preferable that the C content be 0.10% or more. On the other hand, in the case where C is excessively contained, that is, the C content is more than 0.20%, since there is a marked increase in the hardness of a HAZ on the steel sheet side after projection welding has been performed, there is a deterioration in delayed fracture resistance. Therefore, the C content is set to be 0.20% or less. It is preferable that the C content be 0.18% or less.

Si: 0.2% or More and 1.6% or Less

[0069] Since Si is effective for alleviating the distribution of hardness in the thickness direction of a steel sheet by alleviating the segregation of Mn, Si improves delayed fracture resistance after projection welding has been performed. To obtain such an effect, it is necessary that the Si content be 0.2% or more. It is preferable that the Si content be 0.3% or more. However, since there is a deterioration in chemical convertibility in the case where the Si content is excessively high, the Si content is set to be 1.6% or less. It is preferable that the Si content be 1.3% or less.

Mn: 1.0% or More and 3.4% or Less

[0070] Mn contributes to increasing strength through solid solution strengthening and the formation of a second phase. In addition, Mn is an element which is necessary for stabilizing austenite to control a second phase fraction. To obtain such effects, it is necessary that the Mn content be 1.0% or more. On the other hand, in the case where the Mn content is excessively high, when hydrogen enters a steel sheet through an interface between a weld metal zone and a weld heat affected zone after projection welding has been performed, since there is an increase in sliding constraint at grain boundaries, a crack tends to grow at grain boundaries. As a result, there is a deterioration in delayed fracture resistance after projection welding has been performed. Therefore, the Mn content is set to be 3.4% or less. It is preferable that the Mn content be 3.2% or less.

P: 0.05% or Less

[0071] In the case where the P content is excessively high, since inter granular embrittlement occurs due to segregation at grain boundaries becoming marked, there is a deterioration in delayed fracture resistance after projection welding has been performed. Therefore, the P content is set to be 0.05% or less. It is preferable that the P content be 0.03% or less. Here, although there is no particular limitation on the lower limit of the P content, since there is an increase in steel making costs in the case where an attempt is made to achieve ultra-low P content, it is preferable that the P content be 0.005% or more.

S: 0.01% or Less

[0072] In the case where the S content is high, since large amounts of sulfides such as MnS are formed, there is a deterioration in delayed fracture resistance after projection welding has been performed due to MnS becoming a starting point at which a crack is generated at the time of hydrogen entry. Therefore, the upper limit of the S content is set to be 0.01%. It is preferable that the S content be 0.003% or less. Here, although there is no particular limitation on the lower limit of the S content, since there is an increase in steel making costs in the case where an attempt is made to achieve ultra-low S content, it is preferable that the S content be 0.0002% or more.

A1: 0.01% or More and 0.10% or Less

[0073] A1 is an element which is necessary for deoxidization, and it is necessary that the A1 content be 0.01% or more to obtain such an effect. On the other hand, since A1 causes the formation of an excessive amount of ferrite phase after projection welding has been performed, it is difficult to achieve satisfactory peeling strength. Therefore, the upper limit of the A1 content is set to be 0.10%. It is preferable that the A1 content be 0.05% or less.

N: 0.01% or Less

[0074] Since N causes a deterioration in delayed fracture resistance after projection welding has been performed by forming coarse nitrides, it is necessary that the N content be as low as possible. Since there is a marked tendency for forming coarse nitrides in the case where the N content is more than 0.01%, the N content is set to be 0.01% or less. It is preferable that the N content be 0.0075% or less. It is preferable that the N content be 0.0001% or more.

[0075] In the disclosed embodiments, it is necessary that Nb and/or Ti be added in the amounts described below in addition to the constituents described above.

Nb: 0.005% or More and 0.050% or Less

[0076] Since Nb forms fine carbonitrides, Nb improves delayed fracture resistance after projection welding has been performed by decreasing the sizes of hydrogen trap sites and prior austenite grains. To obtain such an effect, the Nb content is set to be 0.005% or more. On the other hand, in the case where the Nb content is high, there is a marked deterioration in the ductility of a base metal, and slab cracking occurs after a continuous casting process. Therefore, the Nb content is set to be 0.050% or less. It is preferable that the Nb content be 0.045% or less or more preferably 0.040% or less.

Ti: 0.005% or More and 0.050% or Less

[0077] Since Ti, like Nb, also forms carbonitrides, Ti improves delayed fracture resistance after projection welding has been performed by decreasing the sizes of hydrogen trap sites and prior austenite grains. To obtain such an effect, the Ti content is set to be 0.005% or more. It is preferable that the Ti content be 0.008% or more. On the other hand, since there is a marked deterioration in the ductility of a base metal in the case where the Ti content is high, the Ti content is set to be 0.050% or less. It is preferable that the Ti content be 0.045% or less.

[0078] In the disclosed embodiments, one, two, or more of the constituents described below may be added as needed in addition to the constituents described above.

B: 0.0050% or Less

[0079] Since B is effective for inhibiting the formation of ferrite and pearlite after projection welding has been performed by improving hardenability, B contributes to improving peeling strength. To obtain such an effect, it is preferable that the B content be 0.0002% or more. On the other hand, since such an effect becomes saturated in the case where the B content is more than 0.0050%, it is preferable that the B content be 0.0050% or less.

Cr: 0.50% or Less

[0080] Cr is an element which contributes to increasing strength by forming a second phase. To obtain such an effect, it is preferable that the Cr content be 0.05% or more. On the other hand, since a plane defect tends to occur due to an excessive amount of martensite being formed in the case where the Cr content is more than 0.50%, it is preferable the Cr content be 0.50% or less. It is more preferable that the Cr content be 0.45% or less.

Mo: 0.50% or Less

[0081] Mo is, like Cr, also an element which contributes to increasing strength by forming a second phase. Moreover, Mo is an element which contributes to improving delayed fracture resistance after projection welding has been performed by increasing hydrogen overpotential. In addition, Mo is an element which contributes to increasing strength by partially forming carbides. To obtain such effects, it is preferable that the Mo content be 0.05% or more. It is more preferable that the Mo content be 0.10% or more. In addition, in the case where the Mo content is more than 0.50%, such effects become saturated, and there is only an increase in cost. Therefore, it is preferable that the Mo content be 0.50% or less. It is more preferable that the Mo content be 0.32% or less.

Co: 0.50% or Less

[0082] Co is, like Mo, also an element which contributes to improving delayed fracture resistance after projection welding has been performed by increasing hydrogen overpotential. To obtain such an effect, it is preferable that the Co content be 0.05% or more or more preferably 0.10% or more. On the other hand, in the case where the Co content is more than 0.50%, such an effect becomes saturated, and there is only an increase in cost. Therefore, it is preferable that the Co content be 0.50% or less. It is more preferable that the Co content be 0.32% or less.

V: 0.05% or Less

[0083] V may contribute to increasing strength by forming fine carbonitrides. To obtain such an effect, it is preferable that the V content be 0.005% or more. On the other hand, in the case where the V content is high and more than 0.05%, there is only a little increase in the effect of increasing strength in relation to an increase in the V content, and there is an increase in alloy cost. Therefore, it is preferable that the V content be 0.05% or less.

Cu: 0.50% or Less

[0084] Cu is an element which contributes to improving delayed fracture resistance after projection welding has been performed by increasing hydrogen overpotential. To obtain such an effect, it is preferable that the Cu content be 0.005% or more. On the other hand, in the case where the Cu content is more than 0.50%, such an effect becomes saturated, and a surface defect tends to occur due to Cu. Therefore, it is preferable that the Cu content be 0.50% or less.

Ni: 0.50% or Less

[0085] Ni is, like Cu, also an element which contributes to improving delayed fracture resistance after projection welding has been performed by increasing hydrogen overpotential. To obtain such an effect, it is preferable that the Ni content be 0.005% or more. In addition, since Ni is effective for inhibiting a surface defect due to Cu from occurring in the case where Ni is added in combination with Cu, Ni is effective in the case where Cu is added. On the other hand, since such effects become saturated in the case where the Ni content is more than 0.50%, it is preferable that the Ni content be 0.50% or less.

Sb: 0.020% or Less

[0086] Since Sb is effective for inhibiting the formation of a decarburized layer in the surface layer of a steel sheet, an electric potential distribution on the steel sheet surface becomes uniform in an aqueous solution, which results in an improvement in delayed fracture resistance after projection welding has been performed. To obtain such an effect, it is preferable that the Sb content be 0.001% or more. On the other hand, in the case where the Sb content is more than 0.020%, since there is an increase in rolling load, there is a deterioration in productivity. Therefore, it is preferable that the Sb content be 0.020% or less.

Ca And/or REM: 0.0050% or Less

[0087] Ca and REM (rare earth metals), which are elements which contribute to improving delayed fracture resistance after projection welding has been performed through the spheroidization of sulfides, may be added as needed. To obtain such an effect, it is preferable that the content be 0.0005% or more in the case where one of such elements is separately added and that the total content be 0.0005% or more in the case where such elements are added in combination. On the other hand, in the case where the total content of Ca and REM is more than 0.0050%, such effect becomes saturated. Therefore, it is preferable that the content be 0.0050% or less in the case where one of such elements is separately added and that the total content be 0.0050% or less in the case where such elements are added in combination.

[0088] The balance of the chemical composition which differs from the constituents described above is Fe and incidental impurities. Examples of the incidental impurities include Sn, Zn, and the like, and it is acceptable that the Sn content be 0.01% or less and that the Zn content be 0.01% or less.

[0089] In addition, in the case where Ta, Mg, and Zr are added within respective ranges for an ordinary steel chemical composition, there is no decrease in the effects of the disclosed embodiments. The acceptable content of each of such elements is 0.01% or less.

[0090] In addition, it is preferable that the nut 1 used in the disclosed embodiments be a nut made of a steel grade having an equivalent carbon content of 0.20% or more, and examples of such a steel grade include S25C (JIS G 4051), SNC815 (JIS G 4102), SNCM630 (JIS G 4103), and SCM440 (JIS G 4105). The equivalent carbon content is calculated by using equation (5) below (JIS G 0203).

[00008]$\begin{array}{cc}\begin{array}{c}\text{equivalent}\text{carbon}\text{content}\left(\%\right)=\text{C}+\text{Mn}/6+\text{Si}/24+\\ \text{Ni}/40+\text{Cr}/5+\text{Mo}/4+\text{V}/14\end{array}& \text{­­­(5)}\end{array}$

[0091] Here, the steel sheet 2 used in the disclosed embodiments may have a Zn-based coating layer (zinc-based coating layer) on the surface thereof as long as the chemical composition of the steel sheet is within the range of the chemical composition of a steel sheet described above. Examples of a steel sheet having a Zn-based coating layer on the surface thereof include a galvanized steel sheet, a galvannealed steel sheet, and an electro-galvanized steel sheet. Here, the Zn-based coating layer may exist on one side of the steel sheet or on both sides of the steel sheet.

[0092] Hereafter, the projection welding method according to the disclosed embodiments will be described.

[0093] The projection welding method according to the disclosed embodiments is a projection welding method for joining the steel sheet 2 and the nut 1 used in the disclosed embodiments by performing projection welding, that is, resistance welding, in which the steel sheet and the nut are clamped, pressurized, and energized between a pair of electrodes. Specifically, it is important that welding conditions are set such that the tensile strength M (MPa) of the steel sheet and the energizing time T (s) of the resistance welding, average welding current K (kA), and pressurizing force F (N) satisfy relational expression (4) below.

[00009]$\begin{array}{cc}0.20\le \left(\left(\text{T}\times \text{K}\right)/4\right)\times {\left(\text{M}/\text{F}\right)}^{1/2}\le 0.75& \text{­­­(4)}\end{array}$

[0094] For example, regarding the preferable ranges of the energizing time T (s) of the resistance welding, average welding current K (kA), and pressurizing force F (N), it is preferable that the energizing time T be 0.10 s to 0.50 s, that the average welding current K be 5 kA to 20 kA, and that the pressurizing force F be 3000 N to 6000 N.

[0095] Here, in relational expression (4), E (expressed in units of s.Math.kA.Math.mm.sup.-1) is defined by the equation E = ((T × K) / 4) × (M / F) .sup.½. This E is also regarded as one of the welding condition factors. In the case where E is less than 0.20, there is a decrease in the area of a region in which the temperature is higher than the A.sub.1 transformation temperature of the steel sheet so that austenite is formed when joining is performed. As a result, since the continuously existing range of the hardened region described above becomes less than 500 .Math.m on at least one of the steel sheet 2 side and the nut 1 side, there is a deterioration in peeling strength after projection welding has been performed. It is more preferable that E be 0.25 or more.

[0096] In addition, in the case where E is more than 0.75, since there is a decrease in cooling rate due to an increase in the amount of heat input, the formation of martensite is inhibited. As a result, since the continuously existing range of the hardened region described above becomes less than 500 .Math.m on at least one of the steel sheet 2 side and the nut 1 side, there is a deterioration in peeling strength after projection welding has been performed. In addition, as a result of holding being performed for a long time in a high temperature range, austenite grains grow. Consequently, since a prior austenite grain size becomes more than 20 .Math.m in the region 5 where the maximum hardness .sub.sHmax on the steel sheet 2 side exists, there is a deterioration in delayed fracture resistance after projection welding has been performed. It is preferable that E be 0.70 or less.

EXAMPLES

[0097] Hereafter, an embodiment of the disclosed embodiments will be described more specifically in accordance with examples.

[0098] However, obviously, the disclosed embodiments are not limited to the examples described below, and the disclosed embodiments may be implemented by appropriately making alterations within a range in accordance with the intent of the disclosed embodiments. Such examples performed in such a way are all within the technical range of the disclosed embodiments.

[0099] After having prepared molten steels having the chemical compositions given in Table 1 and having performed continuous casting to obtain slabs, hot rolling was performed. After having performed pickling followed by cold rolling on the obtained hot rolled steel sheets to obtain cold rolled sheets (having a thickness of 1.4 mm), annealing was performed to manufacture cold rolled steel sheets. In addition, some of the cold rolled steel sheets (steel sheets denoted by sample No. B in Table 2) were made into galvanized steel sheets.

[0100] After having taken a JIS No. 5 tensile test specimen so that the tensile direction was a direction perpendicular to the rolling direction from each of the manufactured steel sheets (i.e., cold rolled steel sheet or galvanized steel sheet), a tensile test was performed (in accordance with JIS Z 2241:1998) to measure tensile strength. The measured results of tensile strength are denoted by M and given in Table 2. In the case of all the steel sheets, the tensile strength was 980 MPa or higher.

[0101] In addition, the peeling strength and delayed fracture resistance after projection welding had been performed were evaluated as described below.

[0102] First, by joining a steel sheet and a nut by performing projection welding, a test specimen (welded body) having a projection weld was manufactured (refer to FIG. 1(c) and FIG. 2(c)). Specifically, a steel sheet test specimen having a size of 50 mm × 150 mm was taken from each of the obtained steel sheets, and a hole having a diameter of 11 mm was punched at the center of the steel sheet test specimen. In addition, an M10 nut for welding having three projection parts was prepared. FIG. 12(a) to FIG. 12(d) are schematic diagrams illustrating this nut for welding, where FIG. 12(a) illustrates the back view of the nut, FIG. 12(b) illustrates the side view of the nut, FIG. 12(c) illustrates the side view of the nut viewed in a direction different from that of FIG. 12(b), and FIG. 12(d) illustrates the cross-sectional view of the projection part of the nut. The steel sheet test specimen and the nut for welding were set on an alternating-current welding machine so that the center of the hole of the steel sheet and the center of the hole of the nut coincided with each other and joined under the welding conditions given in Table 2. The steel grade of the M10 nut for welding described above was S25C (JIS G 4051). The hardness .sub.NH0 of the nut base metal was about 275 HV. As illustrated in FIG. 12(a) to FIG. 12(d), the projection parts 3 were arranged at three positions at equal intervals along the outer circumference of the circular seating surface, and, regarding the shape of the projection part 3 along the outer circumference of the circular seating surface, the projection part 3 had a length of 7 mm, a width of 2.95 mm, and a height of 1.2 mm. The projection part had a height of 1.2 mm and an inclination angle of 45°.

[0103] Regarding the resistance welding conditions, welding was performed by using a resistance welding machine of a single-phase alternating-current type (50 Hz) having a welding gun with a servomotor pressurizing system to manufacture the test specimen (welded body) having a projection weld. Here, a pair of the used electrode chips were flat electrodes having a diameter of 30 mmΦ.

[0104] By fixing a bolt to the hole of the nut of the welded body prepared as described above, a bolt fastening test specimen was prepared. Subsequently, by performing an indentation peeling test in accordance with JIS B 1196:2001 on the obtained bolt fastening test specimen, a load with which the nut was separated from the steel sheet was measured. The measured value of such load was defined as the peeling strength FS. The peeling strength FS measured as described above is given in Table 3.

[0105] In the disclosed embodiments, a case of a peeling strength FS of 9.0 kN or higher is evaluated as a case of excellent peeling strength, and a case of a peeling strength FS of less than 9.0 kN is evaluated as a case of poor peeling strength.

[0106] Delayed fracture resistance was evaluated by manufacturing the bolt fastening test specimen by using the same method as described above. When the peeling strength is defined as FS, a load of 0.7 × FS was applied to the bolt fastening test specimen. Subsequently, by immersing the bolt fastening test specimen in hydrochloric acid solution (pH = 1.5) at room temperature, whether or not the nut was separated from the steel sheet was evaluated. A case where separation did not occur for 100 hours or more was evaluated as a case of good delayed fracture resistance (denoted by symbol “O”), and a case where separation occurred in less than 100 hours was evaluated as a case of poor delayed fracture resistance (denoted by symbol “x”). The evaluation results of delayed fracture resistance obtained as described above are given in Table 3.

[0107] A test for measuring hardness and a test for measuring a prior austenite grain size were performed on a test specimen having a measurement surface which is the cross section of the joined surface as exemplified in FIG. 1(a).

[0108] In a test for measuring hardness, as illustrated in FIG. 1(a), Vickers hardness (HV) was measured in a region from the base metal zone on the nut side (i.e., nut base metal) to the base metal zone on the steel sheet side (i.e., base metal of steel sheet). At this time, measurement was performed under the measurement conditions of a testing force of 0.9807 N and a measurement interval of 0.1 mm.

[0109] The examples of the hardness distribution obtained by a test for measuring hardness are illustrated in FIG. 6 to FIG. 10. The actual measurement data of the hardness distribution of sample Nos. 3 and 4, which are the examples of the disclosed embodiments, are illustrated in FIG. 6 and FIG. 7, respectively, and the actual measurement data of the hardness distribution of sample Nos. 7, 10, and 11, which are the comparative examples, are illustrated in FIG. 8, FIG. 9, and FIG. 10, respectively.

[0110] As illustrated in FIG. 6 to FIG. 10, the vertical axis represents Vickers hardness (HV), and the horizontal axis represents a position (mm) from the joint interface of the weld metal zone. When the joint interface is located at a position of 0.0 mm, the region of the steel sheet is on the plus side, and the region of the nut is on the minus side. The maximum hardness in the hardened region on the nut side is “the maximum hardness .sub.NHmax on the nut side”, and the maximum hardness in the hardened region on the steel sheet side is “the maximum hardness .sub.sHmax on the steel sheet side”. A continuous region which exists on the steel sheet side with respect to the center of the weld metal zone and whose hardness .sub.sH1 is higher than the hardness .sub.sH0 of the base metal of the steel sheet is “the hardened region on the steel sheet side”. A continuous region which exists on the nut side with respect to the center of the weld metal zone and whose hardness .sub.NH1 is higher than the hardness .sub.NH0 of the nut base metal is “the hardened region on the nut side”.

[0111] Regarding other sample numbers, the actual measurement data of a hardness distribution were obtained as in the case of the examples described above. In addition, from such actual measurement data of a hardness distribution, the maximum hardness .sub.NHmax on the nut side, the maximum hardness .sub.sHmax on the steel sheet side, the hardness .sub.NH0 of the nut base metal, and the hardness .sub.3H0 of the base metal of the steel sheet were derived, and the hardness ratio (= .sub.NHmax/.sub.sHmax), the hardened region (on the nut side), and the hardened region (on the steel sheet side) were also derived. Moreover, a region in which the hardness .sub.sH1 on the steel sheet side satisfied relational expression (1) above and a region in which the hardness .sub.NH1 on the nut side satisfied relational expression 2) above were derived. These results are given in Table 3. Here, the hardness .sub.NH0 of the nut base metal and the hardness .sub.sH0 of the base metal of the steel sheet are the hardness before welding was performed.

[0112] A test for measuring a prior austenite grain size was performed as described below. In this test, whether or not the region 5 where .sub.sHmax existed was formed of a martensite microstructure having a prior austenite grain size of 20 .Math.m or less was evaluated.

[0113] After having polished a measurement surface, the polished measurement surface was etched in an etching solution composed of a picric acid saturated aqueous solution to expose prior austenite grain boundaries, the image data of the region 5 where .sub.sHmax existed (refer to FIG. 1(a)) was taken at a magnification of 1500 times. The prior austenite grain size was derived from the obtained image data by using an intercept method, that is, under a condition in which a testing line intersected with 20 or more of prior austenite grains, a value obtained by dividing the entire length of the testing line by the total number of such grains with which the testing line intersected was defined as the prior austenite grain size. The prior austenite grain sizes derived as described above are given in Table 3.

[0114] Incidentally, in the hardened region on the steel sheet side, the prior austenite grain size was similarly measured by using the method described above at three positions whose hardness was less than .sub.sHmax and equal to or higher than (.sub.sHmax × 0.8), and the measured values were smaller than that measured in the region where .sub.sHmax existed.

[0115] As indicated in Table 3, it is clarified that, sample numbers (examples of the disclosed embodiments) which satisfied the range of the disclosed embodiments are superior to sample numbers (comparative examples) which did not satisfy the range of the disclosed embodiments in terms of both peeling strength and delayed fracture resistance.

[0116] Incidentally, FIG. 11 is a diagram illustrating the range of the welding condition E in the range of the disclosed embodiments (E: 0.20 to 0.75) in a graph illustrating the relationship between the welding condition E and peeling strength FS, in which the peeling strength FS given in Table 3 is plotted against the welding condition E given in Table 2. As indicated in FIG. 11, it is clarified that there is a marked decrease in peeling strength FS in the case where E is out of the range of the disclosed embodiments.

[0117] In addition, as indicated in Table 3, it is clarified that, in the case of sample No. 6, that is, the comparative example, since the prior austenite grain size (in detail, the prior austenite grain size in a region which has the center thereof at the position corresponding to the maximum hardness .sub.sHmax and which extends for a distance of 500 .Math.m in a direction parallel to the surface of the steel sheet 2 and a distance of 50 .Math.m in a direction parallel to the thickness direction of the steel sheet 2) was more than 20 .Math.m, delayed fracture resistance was poor (symbol: ×).

TABLE-US-00001 Steel Grade Chemical Composition (mass%) Note C Si Mn P S Al N Nb Ti Others A 0.11 0.65 2.31 0.01 0.001 0.03 0.002 0.006 0.031 B: 0.003, Mo: 0.19, V: 0.02 Example Steel B 0.13 1.26 1.66 0.01 0.001 0.03 0.002 0.015 0.043 Cr: 0.16, Sb: 0.003 Example Steel C 0.10 0.35 1.82 0.01 0.001 0.02 0.003 0.032 0.015 Cu: 0.15, Ni: 0.21, Co: 0.05 Example Steel D 0.18 0.70 3.01 0.01 0.001 0.02 0.002 0.022 0.025 V: 0.03, Ca: 0.001 Example Steel E 0.16 0.65 1.94 0.02 0.001 0.03 0.003 - - - Comparative Steel F 0.15 0.81 2.64 0.01 0.001 0.03 0.003 0.021 0.023 - Example Steel G 0.09 0.50 2.78 0.02 0.002 0.02 0.003 0.034 - - Example Steel H 0.13 1.10 1.90 0.02 0.001 0.03 0.002 - 0.031 - Example Steel I 0.16 0.76 2.28 0.01 0.001 0.03 0.030 0.008 0.016 REM: 0.002 Example Steel

TABLE-US-00002 Sample No. Steel Grade Welding Condition Note Resistance Welding Energizing Time T Steel Sheet Tensile Strength M Average Welding Current K K Pressurizing Force F E* s MPa kA N s.Math.kA.Math.mm.sup.-1 1 A 0.24 1180 16.0 6000 0.43 Example 2 A 0.44 1180 15.0 6000 0.73 Example 3 B 0.32 980 14.0 5000 0.50 Example 4 C 0.28 980 12.0 4000 0.42 Example 5 D 0.22 1470 18.0 6000 0.49 Example 6 E 0.22 1180 12.0 4500 0.34 Comparative Example 7 A 0.10 1180 12.0 5500 0.14 Comparative Example 8 A 0.44 1180 20.0 5500 1.02 Comparative Example 9 A 0.38 1180 20.0 6000 0.84 Comparative Example 10 A 0.50 1180 14.5 6000 0.80 Comparative Example 11 D 0.06 1470 15.0 6000 0.11 Comparative Example 12 C 0.18 980 14.0 6000 0.25 Example 13 F 0.26 1180 14.0 6000 0.40 Example 14 G 0.18 980 16.0 4500 0.34 Example 15 H 0.22 980 17.0 5000 0.41 Example 16 I 0.30 1470 13.0 6000 0.48 Example 17 A 0.50 1180 13.0 6000 0.72 Example 18 C 0.16 980 14.0 5000 0.25 Example *E = ((T × K)/4) ×(M/F).sup.½

TABLE-US-00003 Sample No. Prior Austenite Grain Size Steel Sheet Base Metal Hardness .sub.SH0 Nut Base Metal Hardness .sub.NH0 Maximum Hardness on Steel Sheet Side .sub.SHmax Maximum Hardness on Nut Side .sub.NHmax Hardness Ratio Hardened Region (on Steel Sheet Side) Hardened Region (on Nut Side) Region Where .sub.SH1 ≥ 1.1 × .sub.SH0 Is Satisfied (on Steel Sheet Side) Side) Region Where .sub.NH1 ≥ 1.1 × .sub.NH0 Is Satisfied (on Nut Side) Peeling Strength FS Delayed Fracture Resistance Note .Math.m HV HV HV HV - .Math.m .Math.m .Math.m .Math.m kN 1 12 348 275 449 508 1.13 980 1360 800 1300 10.5 O Example 2 18 348 275 428 441 1.03 960 540 720 520 10.9 O Example 3 10 317 275 436 479 1.10 1050 1480 1010 1450 12.3 O Example 4 12 309 275 449 511 1.14 1000 1320 960 1260 11.5 O Example 5 8 430 275 495 529 1.07 720 1100 580 1060 11.3 O Example 6 21 394 275 476 519 1.09 660 760 520 740 10.1 X Comparative Example 7 8 348 275 456 545 1.20 470 930 440 790 4.3 O Comparative Example 8 21 348 275 411 343 0.83 880 340 640 320 7.6 X Comparative Example 9 21 348 275 402 354 0.88 920 400 740 380 8.1 X Comparative Example 10 21 348 275 406 376 0.93 900 490 840 450 8.3 X Comparative Example 11 8 430 275 530 571 1.08 700 490 630 460 3.9 O Comparative Example 12 12 309 275 443 527 1.19 700 790 520 750 10.2 O Example 13 12 393 275 467 506 1.08 1040 1300 800 1220 11.8 O Example 14 14 323 275 411 515 1.25 900 780 680 760 10.8 O Example 15 13 330 275 419 502 1.20 980 1360 720 1280 11.4 O Example 16 15 452 275 512 529 1.03 1080 1420 820 1320 12.2 O Example 17 18 348 275 418 428 1.02 900 520 700 480 9.3 O Example 18 12 309 275 447 535 1.20 660 760 480 720 9.4 O Example * hardness ratio = (maximum hardness .sub.NHmax on the nut side)/(maximum hardness .sub.sHmax on the steel sheet side)