Patent Application
20200353552
The present invention relates to an are spot welding method.
In the field of automobiles, car bodies are increasingly becoming light-weight as the fuel efficiency is pursued and regulations on exhaust gas are imposed. Under such trends, high-strength steel sheets having a tensile strength exceeding 780 MPa are increasingly employed as the steel sheets used in automobile parts, and it is expected that the trends toward higher strength will continue in the future. Moreover, structural parts, such as car body parts, formed to have complicated shapes are required to have high press formability as well as high strength.
Thus, there is a tendency to use steel sheets with an increased C content in order to meet both of these properties. Meanwhile, resistance spot welding is mostly employed in car body assembly and joining of parts. Although addition of C to the steel sheets is effective for increasing the strength of the steel sheets and improving the press formability, welding heat during the course of resistance spot welding generates martensite in the heat affected zone (HAZ), resulting in excessive hardening and embrittlement. Thus, there has been a problem of significantly degraded weldability, such as degraded strength and generation of cracks.
Meanwhile, are spot welding is known as an alternative welding technique for the resistance spot welding. For example, PTL 1 describes an are spot welded joint obtained by performing are spot welding on high-tensile steel sheets superimposed on each other, and that the strength of the weld metal can be obtained and an arc spot welded joint having a high cross tensile strength and excellent joint strength is obtained by controlling the relationship between the base metal hardness of a high-tensile steel sheet and the weld metal hardness to be in an appropriate range.
There is also known are spot welding that uses a wire having an Fe content of less than 98.5 mass %, which corresponds to a general-purpose wire YGW11, YGW15, YGW18, or YGW19; however, with a steel sheet having a higher C content, this spot are spot welding has had problems in that brittle fracture occurs in the HAZ and sufficient CTS is not obtained.
PTL 1: Japanese Unexamined Patent Application Publication No. 2013-10139
PTL 1 describes that the joint strength can be increased by equalizing the hardness of the weld metal and the hardness of the steel sheet. However, PTL 1 does not take into account the embrittlement of the HAZ. Moreover, general-purpose welding wires such as YGW11, YGW15, YGW18, and YGW19 are used as the welding wire. In such a case, when a steel sheet having a high C content is used as the base metal, embrittlement of the HAZ becomes notable, and brittle fracture is considered to occur without gaining sufficient joint strength.
Thus, an object of the present invention is to provide an are spot welding method with which brittle fracture is prevented and high joint strength can be obtained even when a steel sheet having a high C content is used.
The inventors of the present invention have conducted extensive investigations, found that the object can be achieved by using a welding wire containing a particular amount or more of Fe and adjusting the ratio of the carbon equivalent of the weld metal formed to the carbon equivalent of the steel sheet serving as the base metal to be within a particular range, and thus accomplished the present invention.
In other words, the present invention relates to an are spot welding method that uses a steel sheet having a carbon equivalent CeqBM, which is expressed by formula (1) below, of 0.38 or more, the are spot welding method including using a welding wire containing 98.5 mass % or more of Fe,
wherein CeqWM/CeqBM, which is a ratio of a carbon equivalent CeqWM, which is expressed by formula (2) below, of a weld metal formed to the carbon equivalent CeqBM of the steel sheet, is 0.2 to 1.0:
Ceq
BM=[C]BM+[Mn]BM/6+([Cu]BM+[Ni]BM)/15+([Cr]BM+[Mo]BM+[V]BM)/5 (1)
(where [C]BM, [Mn]BM, [Cu]BM, [Ni]BM, [Cr]BM, [Mo]BM, and [V]BM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the steel sheet)
Ceq
WM=[C]WM+[Mn]WM/6+([Cu]WM+[Ni]WM)/15+([Cr]WM+[Mo]WM+[V]WM)/5 (2)
(where [C]WM, [Mn]WM, [Cu]WM, [Ni]WM, [Cr]WM, [Mo]WM, and [V]WM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the weld metal).
In the arc spot welding method described above, a carbon equivalent CeqW, which is expressed by formula (3) below, of the welding wire may be 0.3 or less:
Ceq
W=[C]W+[Mn]W/6+([Cu]W+[Ni]W)/15+([Cr]W+[Mo]W)/5 (3)
(where [C]W, [Mn]W, [Cu]W, [Ni]W, [Cr]W, and [Mo]W respectively represent C, Mn, Cu, Ni, Cr, and Mo contents (mass %) in the welding wire).
In the arc spot welding method described above, a heat input may be 5.5 kJ or less.
In the arc spot welding method described above, when arc spot welding is performed on a first steel sheet on an arc exposed side and a second steel sheet that are superimposed on top of each other with a rear surface of the first steel sheet facing a front surface of the second steel sheet, and when a bead diameter of the weld metal on a front surface of the first steel sheet is assumed to be r1 and a bead diameter of the weld metal on the front surface of the second steel sheet is assumed to be r2, r1 and r2 may satisfy formula (4) below, and when, in a section of the weld metal taken in a direction parallel to a thickness of the steel sheets so as to pass a center of the weld metal, a region corresponding to the weld metal projecting from the front surface of the first steel sheet is assumed to be a first region, a region corresponding to the weld metal projecting from a rear surface of the second steel sheet is assumed to be a second region, and a region other than the first region and the second region is assumed to be a third region, X expressed by formula (6) below may be 0.2 to 0.8:
0.2≤(r2/r1)≤1.0 (4),
X=(area of first region+area of second region)/(area of first region+area of second region+area of third region) (6).
In the are spot welding method described above, a ratio of a Vickers hardness of the weld metal to a Vickers hardness of the steel sheet (Vickers hardness of weld metal/Vickers hardness of steel sheet) may be 0.3 to 1.2.
According to the arc spot welding method of the present invention, brittle fracture is prevented and high joint strength can be obtained even when a steel sheet having a high C content is used.
The embodiments of the present invention will now be described in detail. It should be understood that the present invention is not limited by the embodiments described above. Moreover, in this description, the percentage (mass %) based on mass has the same meaning as the percentage (wt %) based on weight.
An are spot welding method of this embodiment (hereinafter, may be referred to as the present are spot welding method) is an are spot welding method that uses a steel sheet having a carbon equivalent CeqBM, which is expressed by formula (1) below, of 0.35 or more, the method including using a welding wire containing 98.5 mass % or more of Fe, wherein CeqWM/CeqBM, which is a ratio of a carbon equivalent CeqWM of a weld metal formed expressed by formula (2) below to a carbon equivalent CeqBM of the steel sheet, is 0.2 to 1.0.
Ceq
BM=[C]BM+[Mn]BM/6+([Cu]BM+[Ni]BM)/15+([Cr]BM+[Mo]BM+[V]BM)/5 (1)
(where [C]BM, [Mn]BM, [Cu]BM, [Ni]BM, [Cr]BM, [Mo]BM, and [V]BM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the steel sheet).
Ceq
WM=[C]WM+[Mn]WM/6+([Cu]WM+[Ni]WM)/15+([Cr]WM+[Mo]WM+[V]WM)/5 (2)
(where [C]WM, [Mn]WM, [Cu]WM, [Ni]WM, [Cr]WM, [Mo]WM, and [V]WM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the weld metal).
The carbon equivalent CeqBM of the base metal significantly affects embrittlement of the welding junction, which is the interface between the weld metal and the base metal. Here, when the carbon equivalent CeqBM of the steel sheet is 0.35 or more, martensite is generated near the welding junction. Since martensite is extremely hard with Hv of 700 or more, and is brittle, martensite is a cause of brittle fracture when a load is applied. The present are spot welding method aims to prevent brittle fracture and obtain high joint strength even in such cases, and is thus targeted to the cases in which a steel sheet (hereinafter may be referred to as a high-C steel sheet) having a carbon equivalent CeqBM of 0.35 or more is used as the base metal.
In order to achieve the object described above, in the present are spot welding method, a welding wire containing 98.5 mass % or more of Fe is used. The weld metal formed can be softened by using the welding wire containing 98.5 mass % or more of Fe. In such a case, since the weld metal selectively deforms when stress is applied, it becomes possible to suppress brittle fracture at the welding junction. The Fe content in the welding wire is preferably 99 mass % or more.
Note that the chemical components other than Fe contained in the welding wire are not particularly limited, and examples thereof include optional components such as C, Si, Mn, Cu, Ni, Cr, Mo, B, and Ti, and unavoidable impurities such as S and P.
In the present are spot welding method, CeqWM/CeqBM, which is the ratio of the carbon equivalent CeqWM of the weld metal to the carbon equivalent CeqBM of the steel sheet, is set to be 0.2 to 1.0. At CeqWM/CeqBM less than 0.2, CTS may be degraded due to hot cracking. Thus, CeqWM/CeqBM is 0.2 or more and preferably 0.5 or more. When CeqWM/CeqBM exceeds 1.0, the weld metal may become brittle. Thus, CeqWM/CeqBM is 1.0 or less and preferably 0.7 or less.
In the present are spot welding method, the carbon equivalent CeqW of the welding wire expressed by formula (3) below is preferably 0.3 or less.
Ceq
W=[C]W+[Mn]W/6+([Cu]W+[Ni]W)/15+([Cr]W+[Mo]W)/5 (3)
(where [C]W, [Mn]W, [Cu]W, [Ni]W, [Cr]W, and [Mo]W respectively represent C, Mn, Cu, Ni, Cr, and Mo contents (mass %) in the welding wire).
The reason for this is as follows.
That is, the carbon equivalent CeqW of the welding wire affects embrittlement as significantly as the carbon equivalent CeqBM of the steel sheet. When CeqW exceeds 0.3, martensite occurs in the weld metal, the weld metal becomes brittle, and thus it becomes difficult to obtain sufficient joint strength. Thus, CeqW is preferably 0.3 or less and more preferably 0.2 or less.
In the present are spot welding method, the welding conditions such as heat input and shield gas are not particularly limited, and may be appropriately adjusted within the range that does not obstruct the effects of the present invention.
Although the heat input is not particularly limited, increasing the heat input increases the amount of martensite generated in the welding junction between the base metal and the weld metal and in the HAZ, and accelerates embrittlement; thus, in the present arc spot welding method, the heat input is preferably 5.5 kJ or less and more preferably 2.5 kJ or less. Although the lower limit of the heat input is not particularly limited, from the viewpoint of obtaining a heat input required to melt the lower sheet, the heat input is preferably 1.3 kJ or more, for example.
Referring to
0.2≤(r2/r1)≤1.0 (4),
X=(area of first region+area of second region)/(area of first region+area of second region+area of third region) (6).
Moreover, when the bead diameter of the weld metal 3 on the rear surface 22 of the second steel sheet 2 is assumed to be r3 and formula (5) below is satisfied, a more appropriate joint strength can be obtained, and this is more preferable.
0.5≤(r2/r3)≤10.0 (5)
The shape of the weld metal 3 is a factor that determines where the stress concentrates when a tensile load is applied, and is an important factor that contributes to the position of fracture. Here, r2/r1 in formula (4) and r2/r3 in formula (5) serve as parameters for the fractured part and the fracture propagation direction.
<0.2≤(r2/r1)≤1.0 (4)>
In this embodiment, when r2/r1 is less than 0.2 or exceeds 1.0, such a shape is formed that stress concentrates in the welding junction (weld metal 3-HAZ 4) on the first steel sheet 1 side indicated by point A in
<0.5≤(r2/r3)≤10.0 (5)>
In this embodiment, when r2/r3 is less than 0.5 or exceeds 10.0, such a shape is formed that stress concentrates in the welding junction (weld metal 3-HAZ 4) on the second steel sheet 2 side indicated by point B in
<0.2≤X≤0.8>
As described above, referring to
X=(area of first region 51+area of second region 52)/(area of first region 51+area of second region 52+area of third region 53)
Here, X serves as a parameter for the penetration ratio, which is a factor that contributes to the carbon equivalent and the shape of the weld metal. When X is less than 0.2, the shape of the weld metal does not fall within the ranges defined by formulae (4) and (5) above, and stress concentration occurs at the overlap portion between the upper sheet (first steel sheet) and the lower sheet (second steel sheet). Thus, X is preferably 0.2 or more and more preferably 0.4 or more.
Meanwhile, when X exceeds 0.8, the dilution ratio of the base metal increases, and the components in the steel sheet penetrate into the weld metal; thus, the carbon equivalent CeqWM in the weld metal increases, and embrittlement is accelerated. Moreover, CeqWM/CeqBM defined as above may become outside the range of 0.2 to 1.0. Thus, X is preferably 0.8 or less, more preferably 0.7 or less, and yet more preferably 0.6 or less.
In the present are spot welding method, the ratio of the Vickers hardness of the weld metal to the Vickers hardness of the steel sheet (Vickers hardness of weld metal/Vickers hardness of steel sheet) (hereinafter may be referred to as the hardness ratio) is preferably 0.3 to 1.2.
When the hardness ratio is less than 0.3 and stress is applied, the weld metal selectively undergoes plastic deformation, but the base metal rarely undergoes plastic deformation. Thus, in order for both the base metal and the weld metal to undergo plastic deformation, the hardness ratio is preferably 0.3 or more and more preferably 0.5 or more.
Meanwhile, when the hardness ratio exceeds 1.2, the weld metal is harder than the base metal, and thus the weld metal does not readily undergo plastic deformation. When the weld metal does not plastically deform, the stress concentrates on the welding junction, which is the interface between the weld metal and the base metal. The welding junction is the interface between the base metal structure and the weld metal, and is also a heat affected zone (HAZ) region; thus, the welding junction is brittle. When the hardness ratio exceeds 1.2, fracture occurs from the brittle welding junction as the starting point, and thus high strength is rarely obtained. Thus, the hardness ratio is preferably 1.2 or less, more preferably 1.0 or less, yet more preferably 0.9 or less, and still more preferably 0.8 or less.
The present arc spot welding method may be MAG welding, MIG welding, TIG welding, or any other welding.
The shield gas may be appropriately selected from known gases, such as an inert gas such as Ar and He, CO2, a mixture gas of an inert gas and CO2 and/or O2, and carbon dioxide gas (100% CO2) according to the type of welding, such as MAG welding, MIG welding, and TIG welding; however, from the viewpoint of the weldability, a gas at least containing an inert gas, such as Ar or He, is preferably used.
As described in detail above, according to the arc spot welding method of this embodiment, brittle fracture is prevented and high joint strength can be obtained even when a steel sheet having a high C content is used.
The present invention will now be specifically described through examples below; however, the present invention is not limited by these examples and can be modified within the range that conforms to the gist of the present invention, and implemented. All of such modifications are included in the technical scope of the present invention.
First, the composition, the carbon equivalent CeqBM expressed by formula (1) below, and the Vickers hardness Hv of the steel sheet used are described in Table 1. The Vickers hardness of the steel sheet (BM HV) was measured in accordance with JIS Z 2244.
Ceq
BM=[C]BM+[Mn]BM/6+([Cu]BM+[Ni]BM)/15+([Cr]BM+[Mo]BM+[V]BM)/5 (1)
(where [C]BM, [Mn]BM, [Cu]BM, [Ni]BM, [Cr]BM, [MO]BM, and [V]BM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the steel sheet).
For each example, two steel sheets, which were composed of the steel type and had a thickness shown in Table 2 and which had holes formed therein (holes 204), are arc-spot-welded under the welding conditions shown in Table 2 so as to form a test piece having a shape illustrated in
The welding conditions were a welding current of 200 to 300 A and an arc voltage of 15 to 25 V, and welding was performed at a heat input (kJ) described in Table 2. The heat input is calculated from heat input (kJ)=welding current (A)×arc voltage (v)/1000. In addition, the type of shield gas and the process are also indicated in Table 2. Note that, in the “Process” column, “Pulse”, “Short-circuiting”, “Wire feed control”, “Laser filler”, and “TIG” are defined as follows.
Pulse: Welding was performed under the conditions of base current: 400 A, peak current: 40 A, and peak time: 3.5 msec.
Short-circuiting: Welding was performed by using a DC power supply under conditions of welding current: 230 A and arc voltage: 22 V while repeating a short-circuiting state in which the wire contacts the base metal, and an arc state.
Wire feed control: Welding was performed under the conditions of welding current: 220 A and arc voltage: 22.6 V while conducting wire forward wire feeding and backward feeding according to the welding condition so that backward feeding was conducted when the welding state entered the short-circuiting state and forward feeding was conducted when the welding state entered the arc state.
Laser filler: A YAG laser was used to focus a 4-7 kW laser beam to a diameter of 0.6 to 0.9 mm at a focus distance of 280 mm, and welding was performed at 2 to 6 m/min. The type of the laser serving as the heat source is not particularly limited, and, for example, a carbon dioxide gas laser, a solid-state laser, or the like, may be used.
TIG: TIG welding was performed under the conditions of welding current: 150 A, arc length: 3 mm, filler feed speed: 2 m/min.
The amounts of the wire components in terms of mass % are indicated in Table 2. Moreover, “0” for the wire components in Table 2 indicates that the amount of that component is not more than the amount at which that component is considered to be an unavoidable impurity.
Furthermore, the carbon equivalent CeqW of the wire used in each sample was calculated by using formula (3) below, and is indicated in Table 2.
Ceq
W=[C]W+[Mn]W/6+([Cu]W+[Ni]W)/15+([Cr]W+[Mo]W)/5 (3)
(where [C]W, [Mn]W, [Cu]W, [Ni]W, [Cr]W, and [Mo]W respectively represent C, Mn, Cu, Ni, Cr, and Mo contents (mass %) in the welding wire).
The carbon equivalent CeqBM of the steel sheet is indicated in Table 2, as in Table 1. From the chemical component composition (balance being Fe and unavoidable impurities) of the obtained weld metal shown in Table 2, the carbon CeqWM of the weld metal expressed by formula (2) below was calculated and indicated in Table 2. Furthermore, CeqWM/CeBM, which is the ratio of CeqWM to CeqBM was calculated and indicated in Table 2.
Ceq
WM=[C]WM+[Mn]WM/6+([Cu]WM+[Ni]WM)/15+([Cr]WM+[Mo]WM+[V]WM)/5 (2)
(where [C]WM, [Mn]WM, [Cu]WM, [Ni]WM, [Cr]WM, [Mo]WM, and [V]WM respectively represent C, Mn, Cu, Ni, Cr, Mo, and V contents (mass %) in the weld metal).
When arc spot welding was performed on the first steel sheet 201 on the arc exposed side and the second steel sheet 202 that were superimposed on top of each other with the rear surface 212 of the first steel sheet 201 facing a front surface 221 of the second steel shoot 202, a bead diameter of the weld metal 203 on the front surface 211 of the first steel sheet 201 was assumed to be r1 (mm), a bead diameter of the weld metal 203 on the front surface 221 of the second steel sheet 202 was assumed to be r2 (mm), a bead diameter of the weld metal 203 on a rear surface 222 of the second steel sheet 202 was assumed to be r3 (mm), and r1, r2, and r3 are indicated in Table 3. Moreover, r1/r2 and r3/r2 were calculated and indicated in Table 3.
In a section of the weld metal 203 taken in a direction parallel to the thickness of the steel sheets (first steel sheet 201 and second steel sheet 202) so as to pass a center of the weld metal 203, a region corresponding to the weld metal 203 projecting from the front surface 211 of the first steel sheet 201 was assumed to be a first region, a region corresponding to the weld metal 203 projecting from the rear surface 222 of the second steel sheet 202 was assumed to be a second region, a region other than the first region and the second region was assumed to be a third region, and the area of each region was calculated; furthermore, X expressed by formula (6) below was calculated from the results, and is indicated in Table 3.
X=(area of first region+area of second region)/(area of first region+area of second region+area of third region) (6).
The Vickers hardness (WM Hv) of the weld metal and the Vickers hardness (BM IIv) of the steel sheet serving as the base metal are indicated in Table 3. The Vickers hardness (WM Hv) of the weld metal was measured in accordance with JIS Z 2244 as with measuring the Vickers hardness (BM Hv) of the steel sheet. Furthermore, the ratio (WM Hv/BM Hv) of the Vickers hardness of the weld metal (WM Hv) to the Vickers hardness of the steel sheet (BM Hv) was calculated, and is indicated in Table 3.
Samples 1 to 35 are Examples, and samples 36 to 39 are Comparative Examples.
In sample 36, in which the carbon equivalent CeqBM of the steel sheet was outside the range specified in the present invention, sufficient strength was not obtained in the cross tension testing.
Also in sample 37, in which the Fe content in the welding wire was outside the range specified in the present invention, sufficient strength was not obtained in the cross tension testing.
Also in sample 38, in which the Fe content in the welding wire was outside the range specified in the present invention and CeqWM/CeqBM was outside the range specified in the present invention, sufficient strength was not obtained in the cross tension testing.
Also in sample 39, in which an arc spot welding method was not employed, sufficient strength was not obtained in the cross tension testing.
Meanwhile, samples 1 to 35 that satisfied the requirements specified in the present invention obtained sufficient strength in the cross tension testing.
It is clear to a person skilled in the art that although the present invention has been described in detail by referring to the embodiments, various modifications and alterations are possible without departing from the spirit and the scope of the present invention.
The present application is based on Japanese Patent Application filed on Aug. 4, 2016 (Japanese Patent Application No. 2016-154053), the entire contents of which are incorporated herein by reference.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2016-154053 | Aug 2016 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2017/028023 | 8/2/2017 | WO | 00 |
