WO2023080076A1 - 抵抗スポット溶接部材およびその抵抗スポット溶接方法 - Google Patents

抵抗スポット溶接部材およびその抵抗スポット溶接方法 Download PDF

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WO2023080076A1
WO2023080076A1 PCT/JP2022/040410 JP2022040410W WO2023080076A1 WO 2023080076 A1 WO2023080076 A1 WO 2023080076A1 JP 2022040410 W JP2022040410 W JP 2022040410W WO 2023080076 A1 WO2023080076 A1 WO 2023080076A1
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Prior art keywords
resistance spot
welding
steel
superimposed
steel sheet
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PCT/JP2022/040410
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English (en)
French (fr)
Japanese (ja)
Inventor
央海 澤西
大起 山岸
直雄 川邉
公一 谷口
克利 ▲高▼島
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JFE Steel Corp
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JFE Steel Corp
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Priority to KR1020247012440A priority Critical patent/KR102945885B1/ko
Priority to MX2024004673A priority patent/MX2024004673A/es
Priority to CN202280071201.3A priority patent/CN118139712A/zh
Priority to JP2023504757A priority patent/JP7364113B2/ja
Priority to EP22889896.1A priority patent/EP4393628A4/en
Priority to US18/701,761 priority patent/US20240424596A1/en
Publication of WO2023080076A1 publication Critical patent/WO2023080076A1/ja
Anticipated expiration legal-status Critical
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K11/00—Resistance welding; Severing by resistance heating
    • B23K11/10—Spot welding; Stitch welding
    • B23K11/11—Spot welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K11/00—Resistance welding; Severing by resistance heating
    • B23K11/10—Spot welding; Stitch welding
    • B23K11/11—Spot welding
    • B23K11/115—Spot welding by means of two electrodes placed opposite one another on both sides of the welded parts
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K11/00—Resistance welding; Severing by resistance heating
    • B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
    • B23K11/163—Welding of coated materials
    • B23K11/166—Welding of coated materials of galvanized or tinned materials
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K11/00—Resistance welding; Severing by resistance heating
    • B23K11/24—Electric supply or control circuits therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16B—DEVICES FOR FASTENING OR SECURING CONSTRUCTIONAL ELEMENTS OR MACHINE PARTS TOGETHER, e.g. NAILS, BOLTS, CIRCLIPS, CLAMPS, CLIPS OR WEDGES; JOINTS OR JOINTING
    • F16B5/00—Joining sheets or plates, e.g. panels, to one another or to strips or bars parallel to them
    • F16B5/08—Joining sheets or plates, e.g. panels, to one another or to strips or bars parallel to them by means of welds or the like

Definitions

  • the present invention relates to a member obtained by resistance spot-welding a plurality of steel plates, and more particularly to a resistance spot-welded member suitable as a member for structural parts of automobiles and the like, and a resistance spot welding method therefor.
  • a resistance spot welding method which is a type of lap resistance welding method, is used to join lapped steel sheets.
  • a resistance spot welding method which is a type of lap resistance welding method, is used to join lapped steel sheets.
  • this welding method as shown in FIG. 1, two or more steel plates 1 and 2 are sandwiched between a pair of welding electrodes 8 and 9, and the steel plates are heated by the pair of welding electrodes 8 and 9 from above and below.
  • a high welding current is passed between the upper and lower welding electrodes for a short period of time to join the steel sheets while pressing.
  • FIG. 1 shows a state in which two steel plates are superimposed.
  • a point-like welded portion 4 is obtained by utilizing resistance heat generated by applying a high-current welding current.
  • This point-like welded portion 4 is called a nugget, and is a portion where both steel plates 1 and 2 are melted and solidified at the contact point of the steel plates when an electric current is applied to the superimposed steel plates. are joined in a shape.
  • TSS tensile shear test
  • the surface-treated steel sheet includes galvanizing such as electrogalvanizing and hot-dip galvanizing (including alloyed hot-dip galvanizing), and zinc alloy plating containing elements such as aluminum and magnesium in addition to zinc.
  • galvanizing such as electrogalvanizing and hot-dip galvanizing (including alloyed hot-dip galvanizing)
  • zinc alloy plating containing elements such as aluminum and magnesium in addition to zinc.
  • weld cracks occur when the low-melting-point metal plating layer on the surface of the steel sheet melts during welding, and tensile stress due to the welding electrode pressure, thermal expansion of the steel sheet, and contraction of the steel sheet is applied to the weld. It is believed that cracking is caused by so-called liquid metal embrittlement, in which the molten low-melting-point metal penetrates into the grain boundaries of the base material of the surface-treated steel sheet, reducing the grain boundary strength and causing cracking (hereinafter referred to as (referred to as "LME cracking").
  • LME cracking There are various locations where LME cracks occur, such as the surfaces of the steel plates 1 and 2 on the side in contact with the welding electrodes 8 and 9 and the surfaces of the steel plates 1 and 2 on the side where the steel plates contact each other, as shown in FIG.
  • Patent Document 1 the chemical composition of the steel plate that is a plate set is set to a specific range, specifically, in terms of weight%, C: 0.003 to 0.01%, Mn: 0.05 to 0.5%. , P: 0.02% or less, sol.Al: 0.1% or less, Ti: 48 ⁇ (N / 14) ⁇ 48 ⁇ ⁇ (N / 14) + (S / 32) ⁇ %, Nb: 93 ⁇ (C/12) to 0.1%, B: 0.0005 to 0.003%, N: 0.01% or less, Ni: 0.05% or less, the balance is Fe and unavoidable impurities. is proposed.
  • Patent Document 2 proposes a spot welding method for high-strength plated steel sheets in which spot welding is performed by setting the welding energization time and the holding time after welding energization so as to satisfy the following conditions (1) and (2). ing. 0.25 ⁇ (10 ⁇ t+2)/50 ⁇ WT ⁇ 0.50 ⁇ (10 ⁇ t+2)/50 (1) 300 ⁇ 500 ⁇ t+250 ⁇ t 2 ⁇ HT (2) However, in the conditions (1) and (2), in the conditions (1) and (2), t: plate thickness (mm), WT: welding energization time (ms), HT: holding time after welding energization (ms).
  • Patent Document 2 describes a high-strength galvanized steel sheet in which the energization time and the electrode holding time after energization are appropriately set according to the thickness of the steel sheet, and the amount of alloying elements in the steel sheet is less than a certain level. It has also been proposed to perform spot welding by using
  • the energization pattern is a multi-stage energization of three or more stages, and the appropriate current range ( ⁇ I: a current range that can stably form a nugget having a desired nugget diameter or more and a molten residual thickness of 0.05 mm or more). is 1.0 kA or more, preferably 2.0 kA or more.
  • Patent Document 4 proposes a technique for preventing LME cracking by removing the plating layer of the welded portion prior to spot welding.
  • Patent Document 1 since it is necessary to limit the amount of alloying elements in the steel sheet, there are problems such as the use of steel sheets that satisfy the required performance is restricted. In particular, under the circumstances where high alloying is progressing with the recent steel plate strength increase, its application is extremely limited.
  • Patent Document 2 only proposes a method for suppressing LME cracking when an excessive welding current that causes expulsion is set, and does not mention LME cracking in a state where expulsion does not occur.
  • Patent Document 3 a large number of man-hours are required to optimize the welding conditions, and there was a problem that it could not be applied to steel plates and sheet assemblies for which it was difficult to secure an appropriate current range.
  • Patent Literatures 2 and 3 do not consider the influence of the striking angle of the welding electrode, so there are cases where the countermeasures are inadequate in consideration of the work involved in assembling automobiles.
  • Patent Document 4 manufacturing costs increase because a step of removing the plating layer in advance is required. In addition, since the plating layer is removed, it is thought that the corrosion resistance of the welded portion is lowered.
  • An object of the present invention is to provide a resistance spot-welded member and a resistance spot-welding method thereof, which can manufacture the welded member without removing the plating layer of the Zn-plated steel sheets included in the set.
  • LME cracking occurs when a tensile stress is applied to the steel sheet while the liquid metal such as Zn is in contact with the steel sheet. Therefore, by promoting the alloying of Fe and Zn between the steel plates (between the plates) and setting the Fe concentration in the Zn alloy layer remaining between the plates near the nugget to a certain level or more, tensile stress is applied. Ensure that there is no liquid Zn between the plates at the time point.
  • the inventor of the present invention came up with the idea that LME cracking can be suppressed by this. It was also found that there are suitable welding conditions for keeping the Fe concentration in the Zn alloy layer remaining between the plates above a certain level.
  • a resistance spot welded member in which a plurality of overlapping steel plates are resistance spot welded, At least one of the plurality of superimposed steel sheets is a Zn-plated steel sheet having a Zn-based plating layer on the surface of the steel sheet,
  • the Fe concentration in the Zn alloy layer formed between the steel sheets of the plurality of superimposed steel sheets is C Fe (mass%),
  • L ⁇ m
  • a resistance spot welding member wherein the C Fe and the L satisfy the following formulas (1) and (2).
  • TSmax MPa
  • TSmin MPa
  • C Si shown in the formula (5) is the Si concentration (mass%) of the steel sheet having the highest Si content among the plurality of superimposed steel sheets.
  • the resistance spot welding method for resistance spot welding members according to [6] which satisfies the condition of (a) a state in which the striking angle between the welding electrode and the plurality of superimposed steel plates is 0.2 degrees or more (b) a state in which the amount of misalignment between the pair of welding electrodes is 0.1 mm or more (c) A state in which there is a gap of 0.5 mm or more between any of the welding electrodes and the plurality of superimposed steel plates (d) A gap of 0 between at least one set of steel plates among the plurality of superimposed steel plates .5 mm or more (e) State in which the shortest distance from the center of the welding point to the steel plate end face of the plurality of superimposed steel plates is 10 mm or less [8] Between the main energizing step and the post-energizing step has a non-energizing step for suspending energization, The resistance spot welding method for resistance spot welding members according to [6] or [7], wherein the non-ener
  • the present invention it is possible to suppress LME cracking regardless of the chemical composition of the steel sheet or the combination, particularly in a combination using high-strength steel sheets, and remove the plating layer of the Zn-plated steel sheet included in the combination. It is possible to provide a resistance spot welded member and a welding method thereof that can produce a welded joint without welding.
  • FIG. 1 is a cross-sectional view schematically showing an example of resistance spot welding.
  • FIG. 2 is a cross-sectional view schematically showing a resistance spot welded portion and its periphery in a resistance spot welded member according to one embodiment of the present invention.
  • FIG. 3 is a cross-sectional view schematically showing a resistance spot welded portion and its periphery in a resistance spot welded member according to another embodiment of the present invention.
  • FIG. 4 is a cross-sectional view schematically showing a resistance spot welded portion and its periphery in a resistance spot welded member according to another embodiment of the present invention.
  • FIG. 7 is a cross-sectional view schematically showing an example of crack generation during conventional resistance spot welding.
  • Resistance spot welding parts 2-4, the resistance spot welded member of the present invention will be described.
  • 2 to 4 show, as an example, cross-sectional views in the plate thickness direction in which the resistance spot-welded portion and a part of its surroundings are enlarged in the resistance spot-welded member of the present invention.
  • This enlarged portion is a region surrounded by a square frame shown in FIGS.
  • the present invention is a resistance spot welded member (hereinafter referred to as "welded member") having a resistance spot welded portion in which a plurality of superimposed steel plates are resistance spot welded.
  • welded member a resistance spot welded member
  • at least one of the plurality of superimposed steel sheets is a Zn-plated steel sheet having a Zn-based plating layer on the surface of the steel sheet.
  • the number of steel plates mentioned above is not particularly limited, and may be two or more. Three or more are preferable. Although the upper limit of the number of steel sheets described above is not particularly specified, it is preferable to set the number to 5 or less.
  • the example shown in FIG. 2 is a welded member 6 in which two steel plates are overlapped and welded, and both the steel plate 2 (lower plate) arranged on the lower side and the steel plate 1 (upper plate) arranged on the upper side or Either is a Zn-plated steel sheet.
  • a resistance spot welded portion 4 described below is formed on a steel plate mating surface (overlapping surface) 7 where the steel plates 1 and 2 are in contact.
  • FIGS. 3 and 4 show a welded member 6 in which three steel plates are superimposed and welded.
  • the welding member 6 in FIGS. 3 and 4 includes a steel plate 2 (lower plate) arranged on the lowermost side, a steel plate 1 arranged on the uppermost side (upper plate), and a steel plate 3 arranged between them (middle plate). All or at least one of the plates) is a Zn-plated steel sheet.
  • the resistance spot welds described below are included to include the overlapping surfaces 7 (7a, 7b) where the lower plate 2 and middle plate 3 and the middle plate 3 and upper plate 1 meet. 4 is formed.
  • FIG. 5 and 6 show the Fe concentration (C Fe ) of the Zn alloy layer formed between the steel plates and the nugget edge in the resistance spot welded portion (hereinafter referred to as the “welded portion”) of the welded member of the present invention.
  • the vertical axis is the Fe concentration (mass%)
  • the horizontal axis is the distance ( ⁇ m) from the nugget edge.
  • welded members joints 1 to 8 were prepared by overlapping two or three steel plates and welding them under various welding conditions.
  • C Si mass%
  • the measurement of C Fe of each joint the measurement of the distance L, and the evaluation of LME cracking were performed by the method described in Examples below.
  • LME cracking occurs when a tensile stress is applied to the steel sheet while liquid metal such as Zn is in contact with the steel sheet. Therefore, in the present invention, it is important to promote the alloying of Fe and Zn between the plates and keep the Fe concentration in the Zn alloy layer remaining between the plates in the vicinity of the nugget above a certain level. This ensures that no liquid Zn exists between the plates when the tensile stress is applied.
  • the Fe concentration increases as the distance from the nugget edge to the Fe concentration measurement point decreases. This is because the closer to the nugget, the higher the maximum temperature reached during welding, which promotes alloying.
  • the joints with significant LME cracking that is, the joints rated F (joints 4 and 8) both have a low Fe concentration in the region where the distance from the nugget end is 500 ⁇ m or less.
  • the Fe concentration threshold required to obtain the evaluation A for completely suppressing LME cracking increased.
  • the maximum temperature reached during welding is particularly high, and Zn tends to exist as a liquid phase between the plates when tensile stress occurs after the completion of energization. be. Therefore, by increasing the Fe concentration of the Zn alloy layer formed between the plates at a distance of 500 ⁇ m or less from the nugget end to 20 mass% or more, the melting point of the Zn alloy layer increases, and tensile stress is applied to the weld. It becomes difficult for Zn to exist as a liquid phase when generated. In addition, as mentioned above, the closer the nugget is, the higher the maximum temperature reaches. can prevent the existence of As a result, it was found that LME cracking can be suppressed even in welded members containing Zn-plated steel sheets.
  • FIG. 2 will be used in the following description because the same applies to the case of a plate set in which two steel plates are stacked and in the case of a plate set in which three or more steel plates are stacked.
  • the weld 4 has a nugget 4a and a heat affected zone (HAZ) 4b.
  • a Zn alloy layer 5 is formed outside the nugget end portion and between the plurality of steel plates 1 and 2 (between the plates).
  • the Fe concentration in the Zn alloy layer 5 formed between the stacked steel sheets is C Fe (mass%)
  • the distance from the nugget edge to the C Fe measurement position is L ( ⁇ m )
  • the C Fe and the L satisfy the following relationships (1) and (2).
  • C Fe is less than 20 (mass%)
  • alloying of Fe—Zn between plates is insufficient, increasing the possibility that liquid Zn exists between plates near the nugget.
  • C Fe in formula (1) is set to 20 (mass%) or more.
  • C Fe is preferably 30 (mass%) or more, more preferably 40 (mass%) or more.
  • the upper limit of C Fe in formula (1) is not specified. This is because the larger C Fe is, the higher the melting point of the Zn alloy layer is, which is effective for suppressing LME cracking.
  • C Fe in formula (1) is preferably 98 (mass%) or less, more preferably 95 (mass%) or less.
  • the positional relationship among the nugget edge, the C Fe measurement position, and the distance L from the nugget edge to the C Fe measurement position is as shown in FIG.
  • the “nugget edge” refers to the intersection point between the nugget 4a and the overlapping surfaces 7 of the steel plates 1 and 2.
  • the “C Fe measurement position” refers to the position outside the nugget edge and at the center of the Zn alloy layer 5 in the plate thickness direction.
  • the “C 2 Fe measurement positions (point A shown in FIG. 2)” are present outside both ends of the nugget 4a.
  • the concentration of C 2 Fe and the distance L described above can be measured by the methods described in the examples below.
  • the Fe concentration is measured using the center of the Zn alloy layer in the thickness direction that has moved a certain distance from the nugget end as a measurement point, and in addition, measurements are also performed at positions separated by 1 ⁇ m above and below in the thickness direction.
  • C Fe be the average value of the Fe concentrations at these three points.
  • a Zn alloy layer is formed between the upper plate and the intermediate plate and between the intermediate plate and the lower plate. C Fe between the upper plate and the middle plate and between the middle plate and the lower plate are obtained by the above method, and the minimum value of them is defined as C Fe . The same applies when the number of steel plates is four or more.
  • At least one of the stacked steel sheets is a Zn-plated steel sheet.
  • LME cracking is due to a phenomenon that occurs when at least one Zn-plated steel sheet is used.
  • all the steel sheets of the plurality of superimposed steel sheets may be Zn-plated steel sheets, or a Zn-plated steel sheet and a steel sheet having no metal plating layer may be superimposed. In either case, the effect of the present invention can be obtained.
  • the "Zn-plated steel sheet" in the present invention refers to zinc plating represented by electrogalvanizing and hot-dip galvanizing (including alloyed hot-dip galvanizing), and zinc alloys containing elements such as aluminum and magnesium in addition to zinc. It refers to a steel sheet having a Zn-based plating layer such as plating on the surface of a base steel sheet that is a base material.
  • the composition in the plating layer is not particularly limited, but the Fe concentration in the plating layer is preferably 5 mass % or more in order to increase C 2 Fe . Moreover, from the viewpoint of preventing deterioration of the powdering property of the steel sheet, the Fe concentration in the coating layer is preferably 20 mass % or less.
  • the steel plates used for the plate assembly can have the following configurations as necessary.
  • the Si concentration (C Si ) of the steel sheet with the highest Si content in the set of plates, the Fe concentration (C Fe ) in the Zn alloy layer, and the distance L satisfy the relationship of formula (3) is preferred.
  • the melting point of the Zn alloy layer increases as the C Fe increases, which is effective for suppressing LME cracking, so the upper limit of the formula (3) is not particularly defined for the same reason as the above formula (1).
  • C Fe in the formula (3) is preferably 98 (mass%) or less, more preferably 95 (mass%) or less.
  • C Si , C Fe and L satisfy the following relational expression in the presence of a plate assembly or construction disturbance that easily causes LME cracking.
  • the concentration of C Si can be measured by the method described in Examples below.
  • At least one of the plurality of steel plates that are superimposed has a tensile strength of 980 MPa or more.
  • the tensile strength of the steel sheet is preferably 3000 MPa or less.
  • the tensile strength of the steel sheet having the highest tensile strength among the above-mentioned superimposed steel sheets is TSmax (MPa)
  • the tensile strength of the steel sheet having the lowest tensile strength is TSmin (MPa)
  • FIG. 3 and FIG. 4 show a case where the number of sheets of a plurality of steel plates that are superimposed is three.
  • the lower plate 2 and the intermediate plate 3 are unplated steel plates
  • the upper plate 1 is a plated steel plate.
  • the Zn alloy layer 5 and the above-mentioned C Fe are formed between the upper plate 1 and the intermediate plate 3 .
  • FIG. 4 is an example in which the upper plate 1 has a lower melting point than the middle plate 3 and the lower plate 2 .
  • the outline of the nugget 4a may not be elliptical. In that case, as shown in FIG. The distance L is measured with the farthest position in the direction as the nugget edge. This is the same when two sheets are stacked.
  • the chemical composition of the high-strength steel sheet used in the present invention is not particularly limited as long as it can have the above-described structure. From the viewpoint of applying the present invention to automobile structural parts, it is preferable to use the following component composition.
  • “%” in component composition means “% by mass” unless otherwise specified.
  • C 0.1-0.4% C is an element that contributes to increasing the strength of the steel sheet. Therefore, the C content is preferably 0.1% or more. More preferably, it is 0.12% or more. On the other hand, an excessive addition of C causes excessive hardening of the weld zone, resulting in a decrease in the toughness of the weld zone. Therefore, the C content is preferably 0.4% or less. More preferably, it is 0.38% or less.
  • Si 0.02-2.5%
  • Si is an effective element for improving the strength and elongation of steel sheets. Therefore, the Si content is preferably 0.02% or more. More preferably, it is 0.1% or more.
  • the Si content is preferably 2.5% or less. More preferably, it is 2.0% or less.
  • Mn 1.0-5.0%
  • Mn is an element that contributes to increasing the strength of the steel sheet. Therefore, the Mn content is preferably 1.0% or more. More preferably, it is 1.2% or more.
  • the Mn content is preferably 5.0% or less. More preferably less than 3.5%.
  • the P content is preferably 0.05% or less. More preferably, it is 0.02% or less. There is no particular lower limit for the P content, but extremely low P increases the steelmaking cost, so the P content is preferably 0.005% or more.
  • the S content is preferably 0.01% or less. More preferably, it is 0.005% or less. Although the lower limit of the S content is not specified, extremely low S increases the steelmaking cost. Therefore, the S content is preferably 0.0002% or more.
  • Al 0.01-1.00%
  • Al is an element necessary for deoxidation, and its content is preferably 0.01% or more in order to obtain this effect.
  • excessive addition of Al increases inclusions in the steel sheet, lowers the local deformability, and lowers the ductility of the steel sheet. Therefore, it is preferable to set the upper limit to 1.00%. More preferably, it is 0.80% or less.
  • N 0.01% or less N forms coarse nitrides, which lowers the local deformability and the ductility of the steel sheet. Since this tendency becomes remarkable when the N content is 0.01% or more, the N content is preferably less than 0.01%. More preferably, it is 0.0075% or less. Although the lower limit of the N content is not particularly specified, extremely low N content increases the steelmaking cost. Therefore, the N content is preferably 0.0001% or more.
  • the balance other than the above is Fe and unavoidable impurities.
  • unavoidable impurities include Co, Sn, Zn, etc.
  • the allowable ranges for these contents are Co: 0.05% or less, Sn: 0.01% or less, Zn: 0.01%. It is below. Further, in the present invention, even if Ta, Mg, and Zr are contained within the normal steel composition range, the effect is not lost.
  • each of the following components may be contained.
  • each of the following components may be 0%.
  • Nb 0.1% or less Nb is effective for precipitation hardening of steel sheets by forming fine carbonitrides. In order to obtain the effect, it is preferable to contain 0.005% or more of Nb. On the other hand, if a large amount of Nb is added, not only does the elongation remarkably decrease, but also slab cracking occurs after continuous casting. It is more preferably 0.07% or less, still more preferably 0.055% or less.
  • Ti 0.1% or less Ti is effective for precipitation hardening of steel sheets by forming fine carbonitrides. In order to obtain the effect, it is preferable to contain 0.005% or more of Ti. On the other hand, if a large amount of Ti is added, the elongation is remarkably lowered, so the Ti content is preferably 0.1% or less. It is more preferably 0.065% or less.
  • V 0.05% or less V is effective for precipitation hardening of steel sheets by forming fine carbonitrides. In order to have such effects, it is preferable to add V in an amount of 0.005% or more. On the other hand, even if a large amount of V is added, the strength-increasing effect of the amount exceeding 0.05% is small, and furthermore, the alloy cost increases. Therefore, the V content is preferably 0.05% or less.
  • Cr 1.0% or less Cr is an element that contributes to increasing the shear tensile strength because it tends to form martensite in resistance welds. In order to exhibit this effect, it is preferable to contain 0.05% or more. On the other hand, if the content exceeds 1.0%, planar defects tend to occur, so the content is preferably 1.0% or less. Preferably, it is 0.8% or less.
  • Mo 0.5% or less
  • Mo also tends to form martensite in resistance welds, so it is an element that contributes to increasing the shear tensile strength.
  • the content is preferably 0.5% or less. More preferably, it is 0.42% or less.
  • Cu 1.0% or less
  • Cu is an element that contributes to solid-solution strengthening of the steel sheet. In order to exhibit these effects, it is preferable to contain 0.005% or more. On the other hand, even if the content exceeds 1.0%, the effect is saturated and surface defects due to Cu are likely to occur, so the content is preferably 1.0% or less.
  • Ni 0.50% or less
  • Ni is an element that contributes to increasing the strength of the steel sheet by solid-solution strengthening and transformation strengthening. In order to exhibit these effects, it is preferable to contain 0.005% or more.
  • Cu when Cu is added at the same time, it has the effect of suppressing surface defects caused by Cu, so it is effective when Cu is added.
  • the content is preferably 0.50% or less.
  • B 0.010% or less B is an element that improves the hardenability of the steel sheet and contributes to high strength. In order to exhibit this effect, it is preferable to contain 0.0002% or more. On the other hand, even if the content exceeds 0.010%, the effect is saturated, so the content is preferably 0.010% or less. Preferably, it is 0.008% or less.
  • Sb 0.20% or less
  • Sb has the effect of suppressing the formation of a decarburized layer on the surface layer of the steel sheet, so it can suppress the reduction of martensite on the surface of the steel sheet.
  • the content is preferably 0.001% or more.
  • Sb is added by more than 0.20%, the rolling load is increased and productivity is lowered.
  • Ca and/or REM 0.02% or less
  • Ca and REM rare earth metal are elements that contribute to the improvement of delayed fracture resistance by making the shape of sulfides spherical, and are added as necessary. can be done. In order to exhibit these effects, it is preferable to contain 0.0005% or more of each. On the other hand, even if the content exceeds 0.02%, the effect saturates, so the content is preferably 0.02% or less.
  • Resistance spot welding method Next, one embodiment of the resistance spot welding method for manufacturing the welded member of the present invention will be described.
  • the welding member of the present invention is produced by resistance spot welding in which a plate set in which a plurality of steel plates, including at least one of the Zn-plated steel plates, are superimposed is sandwiched between a pair of welding electrodes, and is joined by energizing while applying pressure. manufactured.
  • a sheet assembly may be made by using a steel sheet (GI or GA) having a Zn-based plating layer and a steel sheet (high-strength cold-rolled steel sheet) having no plating layer. In this case, they are superimposed so that the side having the Zn-based plating layer is in contact with the high-strength cold-rolled steel sheet.
  • a welding device that has a pair of upper and lower welding electrodes and can arbitrarily control the applied pressure and the welding current during welding can be used.
  • the pressure mechanism air cylinder, servomotor, etc.
  • type stationary type, robot gun, etc.
  • welding electrode shape, etc. of the welding device are not particularly limited.
  • the shape of the tip of the welding electrode includes, for example, DR type (dome radius type), R diameter (radius type), D type (dome shape), etc. described in JIS C 9304:1999.
  • the tip diameter of the welding electrode is, for example, 4 mm to 16 mm.
  • the radius of curvature of the tip of the welding electrode is, for example, 10 mm to 400 mm.
  • the present invention can be applied to both direct current and alternating current. For alternating current, "current" means "rms current.”
  • the resistance spot welding of the present invention includes a main current-applying step for forming a nugget and a post-current-applying step for performing a post-heat treatment after forming the nugget.
  • Im (kA) be the average current value in the main energizing step
  • Ip (kA) be the average current value in the post-energizing step
  • tp (ms) be the total energizing time in the post-energizing step
  • the current value and the current application time (Im, Ip and tp) in the main current application step and the post-current application step and the Si content (C Si ) of the steel sheet are set so as to satisfy the relationship of the formula (5). Control welding conditions.
  • Im, Ip, tp and C Si satisfy the following relational expressions in the presence of plate assembly or construction disturbance that easily causes LME cracking.
  • the alloying of the Zn alloy layer between the plates is promoted, which is effective for increasing CFe . No value is specified.
  • the value of ((Ip/Im) 2 ⁇ tp) shown in equation (5) is set to (300 ⁇ C Si +3700) or less.
  • the current values in the main energization step and the post-energization step satisfy the relationship Ip/Im ⁇ 2.0.
  • Ip/Im the current values in the main energization step and the post-energization step satisfy the relationship Ip/Im ⁇ 2.0.
  • the above (Ip/Im) is preferably 1.8 or less.
  • the above (Ip/Im) is preferably 0.5 or more, more preferably 0.9 or more, and still more preferably 1.0 or more.
  • the total energization time in the post-energization process is preferably 50 to 1000 ms in order to obtain a certain amount of heat input and prevent an excessive increase in the tact time of the automobile manufacturing process.
  • the hold time after the post-energization process shall be 20-1000 ms. This suppresses the occurrence of blowholes in the nugget and an excessive increase in tact time.
  • the present invention may have the following welding conditions in addition to the welding conditions in the above steps.
  • one or more states selected from the following (a) to (e) are applied to at least one welding point immediately before applying pressure by the welding electrode. preferably fulfilled. Thereby, the effects of the present invention can be obtained more effectively.
  • a state in which the striking angle between the welding electrode and the plurality of steel plates that are superimposed is 0.2 degrees or more. angle formed with the thickness direction”.
  • the striking angle is large, bending stress is applied to the weld zone, causing large compressive plastic deformation locally and increasing the tensile stress after cooling.
  • the effect of the present invention can be effectively obtained when the hitting angle is 0.2 degrees or more. If the hitting angle is too large, the nugget formation becomes unstable, which causes the occurrence of expulsion. Therefore, the hitting angle is preferably 10 degrees or less.
  • the hitting angle is more preferably 1 degree or more, more preferably 8 degrees or less.
  • Misalignment means a state in which the central axes of a pair of welding electrodes are not aligned. As with the hit angle described above, when the misalignment is large, bending stress is applied to the welded portion, and LME cracking is likely to occur. When the amount of misalignment is 0.1 mm or more, the effects of the present invention can be effectively obtained. If the amount of misalignment is too large, nugget formation becomes unstable and causes expulsion. Therefore, the amount of misalignment is preferably 5 mm or less. The misalignment amount is more preferably 0.2 mm or more, more preferably 3 mm or less.
  • (c) A state in which there is a gap of 0.5 mm or more between any welding electrode and a plurality of superimposed steel plates.
  • the movable electrode When one electrode is movable (hereinafter referred to as the movable electrode) and the other electrode is fixed (hereinafter referred to as the fixed electrode), if there is a gap between the fixed electrode and the steel plate, the pressure from the movable electrode will be When started, bending stress is applied to the weld because the steel plate undergoes bending deformation. This makes it easier for LME cracks to occur.
  • the effect of the present invention can be effectively obtained when the gap between the welding electrode and the steel plate is 0.5 mm or more. If this gap amount is too large, the nugget formation becomes unstable, which causes expulsion. Therefore, this gap amount is preferably 5 mm or less.
  • the amount of the gap is more preferably 1 mm or more, more preferably 3 mm or less.
  • gap between one or more sets of steel plates means that, in two or more superimposed steel plates, when two steel plates arranged in the vertical direction are regarded as one set, there is a gap between one or more sets of steel plates. means that there is a gap in
  • the effect of the present invention can be effectively obtained when the shortest distance from the center of the welding point to the steel plate end surface is 10 mm or less.
  • the shortest distance is less than 3 mm, the occurrence of expulsion during welding becomes significant, and the nugget diameter tends to vary, which destabilizes the strength of the welded portion. Therefore, it is preferable that the shortest distance is 3 mm or more. This shortest distance is more preferably 4 mm or more, more preferably 8 mm or less.
  • the present invention it is preferable to provide a no-energization step between the main current-applying step and the post-energizing step. Thereby, the vicinity of the nugget can be kept within a constant temperature range.
  • the non-energization time in the non-energization step is preferably 10 to 350 ms. Note that when the non-energization time is repeated, the total non-energization time is preferably 2000 ms or less from the viewpoint of suppressing an increase in tact time.
  • the number of repetitions of the non-energization process and the post-energization process is preferably 2 or more, more preferably 4 or more.
  • the upper limit of the number of repetitions is not particularly defined, there is generally an upper limit to the number of repetitions that can be set in welding equipment, and setting the number of repetitions exceeding the upper limit requires modification of the welding equipment. Therefore, the number of times is preferably 20 times or less, more preferably 10 times or less, because the equipment cost in the automobile manufacturing process increases.
  • the pressurizing conditions in each step are not particularly limited. From the viewpoint of automotive applications, it is preferable to adjust the pressurization conditions in the range of 2.0 to 8.0 kN.
  • a welded joint (welded member) was produced under the welding conditions shown in Table 2.
  • a servomotor pressurized, single-phase alternating current (50 Hz) resistance welder attached to a welding gun was used as the welding device.
  • the pair of electrode tips used were chromium-copper DR-type electrodes having a tip radius of curvature R of 40 mm and a tip diameter of 6 mm.
  • the set of plates was arranged in the order of steel plate 1, steel plate 2, and steel plate 3 shown in Table 1 from the upper side and superimposed.
  • "GA” shown in the plating column of Table 1 refers to a steel sheet having an alloyed hot-dip galvanized layer
  • "GI” refers to a steel sheet having a hot-dip galvanized layer
  • "EG” has an electro-galvanized layer. It refers to a steel sheet
  • "none” refers to a steel sheet (cold-rolled steel sheet) that does not have a coating layer.
  • the symbols shown in the "work disturbance” column of Table 2 correspond to (a) to (e) shown in the welding work disturbance described above.
  • tp (ms) shown in the welding conditions in Table 2 is the sum of the energization times in the post-energization process, and "-" shown in the non-energization process indicates that there is no non-energization process.
  • the "number of repetitions of the non-energization process/post-energization process” shown in the welding conditions in Table 2 indicates the number of times the non-energization process and the post-energization process are repeated after the main current process when the non-energization process is included.
  • main energization process-post-energization process the number of repetitions is "0", and in the case of “main energization process-non-energization process-post-energization process”, the repetition number is "1". Also, for example, when the number of repetitions is "3", "main energization process - non-energization process (1) - post-energization process (1) - non-energization process (2) - post-energization process (2) - non-energization process (3)-post-energization process (3)”.
  • the "Si content” column in Table 1 shows the Si concentration of each steel sheet
  • the "Mn content” column shows the Mn concentration of each steel sheet
  • the "C Si " column in Tables 1 and 2. shows the Si concentration of the steel sheet with the highest Si content in the set.
  • “C Si” was measured by inductively coupled plasma (ICP) optical emission spectroscopy.
  • tensile strength column of Table 1 a JIS No. 5 tensile test piece was taken from each steel plate in the rolling direction, and the tensile strength (MPa) measured by performing a tensile test in accordance with JIS Z 2241 is shown. show.
  • the "TSmax” column in Tables 1 and 2 shows the maximum tensile strength of the steel plate in the plate assembly measured in the tensile test
  • the "TSmin” column shows the tensile strength in the plate assembly measured in the tensile test. Shows the tensile strength of the smallest steel plate.
  • the following methods were used to evaluate the LME cracking of the weld, measure the Fe concentration (C Fe ) in the Zn alloy layer, and measure the distance L from the nugget edge to the C Fe measurement point. was measured.

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2025121278A1 (https=) * 2023-12-08 2025-06-12
JPWO2025121277A1 (https=) * 2023-12-08 2025-06-12
WO2026014321A1 (ja) * 2024-07-10 2026-01-15 Ｊｆｅスチール株式会社 スポット溶接部材、スポット溶接部材用鋼板およびスポット溶接部材の製造方法
WO2026014320A1 (ja) * 2024-07-10 2026-01-15 Ｊｆｅスチール株式会社 スポット溶接部材、スポット溶接部材用鋼板およびスポット溶接部材の製造方法

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* Cited by examiner, † Cited by third party
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10195597A (ja) 1996-11-14 1998-07-28 Sumitomo Metal Ind Ltd 接合性に優れた薄鋼板
JP2003103377A (ja) 2001-09-27 2003-04-08 Nippon Steel Corp 高強度めっき鋼板のスポット溶接方法
JP2003236676A (ja) 2002-02-19 2003-08-26 Jfe Steel Kk 高張力亜鉛系めっき鋼板のスポット溶接方法
WO2016159169A1 (ja) 2015-03-30 2016-10-06 新日鐵住金株式会社 めっき鋼板のスポット溶接方法
JP2017510702A (ja) * 2013-12-25 2017-04-13 ポスコＰｏｓｃｏ 耐液体金属脆化割れ性に優れた溶融亜鉛めっき鋼板
JP2018039019A (ja) * 2016-09-05 2018-03-15 新日鐵住金株式会社 スポット溶接方法
JP2021079416A (ja) * 2019-11-20 2021-05-27 トヨタ自動車株式会社 抵抗スポット溶接方法

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA2912591C (en) * 2013-06-05 2017-12-19 Nippon Steel & Sumitomo Metal Corporation Spot-welded joint and spot welding method
JP7059572B2 (ja) * 2017-11-10 2022-04-26 日本製鉄株式会社 溶接継手の製造方法及び溶接継手
EP3736076B1 (en) * 2018-02-09 2022-08-24 JFE Steel Corporation Resistance spot welding method, and method for producing resistance-spot-welded joint
JP7047535B2 (ja) 2018-03-29 2022-04-05 日本製鉄株式会社 抵抗スポット溶接方法
JP2020082105A (ja) * 2018-11-19 2020-06-04 株式会社神戸製鋼所 接合構造体及び接合構造体の製造方法
JP7352060B2 (ja) 2019-03-20 2023-09-28 日本製鉄株式会社 溶接構造体及びその製造方法

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10195597A (ja) 1996-11-14 1998-07-28 Sumitomo Metal Ind Ltd 接合性に優れた薄鋼板
JP2003103377A (ja) 2001-09-27 2003-04-08 Nippon Steel Corp 高強度めっき鋼板のスポット溶接方法
JP2003236676A (ja) 2002-02-19 2003-08-26 Jfe Steel Kk 高張力亜鉛系めっき鋼板のスポット溶接方法
JP2017510702A (ja) * 2013-12-25 2017-04-13 ポスコＰｏｓｃｏ 耐液体金属脆化割れ性に優れた溶融亜鉛めっき鋼板
WO2016159169A1 (ja) 2015-03-30 2016-10-06 新日鐵住金株式会社 めっき鋼板のスポット溶接方法
JP2018039019A (ja) * 2016-09-05 2018-03-15 新日鐵住金株式会社 スポット溶接方法
JP2021079416A (ja) * 2019-11-20 2021-05-27 トヨタ自動車株式会社 抵抗スポット溶接方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4393628A4

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2025121278A1 (https=) * 2023-12-08 2025-06-12
JPWO2025121277A1 (https=) * 2023-12-08 2025-06-12
WO2025121278A1 (ja) * 2023-12-08 2025-06-12 Ｊｆｅスチール株式会社 抵抗スポット溶接部材およびその抵抗スポット溶接方法
WO2025121277A1 (ja) * 2023-12-08 2025-06-12 Ｊｆｅスチール株式会社 抵抗スポット溶接部材およびその抵抗スポット溶接方法
JP7831701B2 (ja) 2023-12-08 2026-03-17 Ｊｆｅスチール株式会社 抵抗スポット溶接部材およびその抵抗スポット溶接方法
JP7831700B2 (ja) 2023-12-08 2026-03-17 Ｊｆｅスチール株式会社 抵抗スポット溶接部材およびその抵抗スポット溶接方法
WO2026014321A1 (ja) * 2024-07-10 2026-01-15 Ｊｆｅスチール株式会社 スポット溶接部材、スポット溶接部材用鋼板およびスポット溶接部材の製造方法
WO2026014320A1 (ja) * 2024-07-10 2026-01-15 Ｊｆｅスチール株式会社 スポット溶接部材、スポット溶接部材用鋼板およびスポット溶接部材の製造方法
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