JP2006224150A - Resistance spot welding method for different materials - Google Patents
Resistance spot welding method for different materials Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 49
- 238000000034 method Methods 0.000 title claims abstract description 26
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 57
- 239000010959 steel Substances 0.000 claims abstract description 57
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 55
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 55
- 238000007747 plating Methods 0.000 claims abstract description 32
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- 239000000956 alloy Substances 0.000 claims abstract description 8
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 7
- 239000011701 zinc Substances 0.000 claims abstract description 7
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910001297 Zn alloy Inorganic materials 0.000 claims description 4
- 229910045601 alloy Inorganic materials 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 5
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 239000010410 layer Substances 0.000 description 42
- 229910018084 Al-Fe Inorganic materials 0.000 description 12
- 229910018192 Al—Fe Inorganic materials 0.000 description 12
- 239000000428 dust Substances 0.000 description 11
- 229910002056 binary alloy Inorganic materials 0.000 description 8
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- 230000008018 melting Effects 0.000 description 3
- 229910002058 ternary alloy Inorganic materials 0.000 description 3
- 229910000680 Aluminized steel Inorganic materials 0.000 description 2
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- 238000001816 cooling Methods 0.000 description 2
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- 238000013021 overheating Methods 0.000 description 2
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- 238000009864 tensile test Methods 0.000 description 2
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000005219 brazing Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
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- 239000011247 coating layer Substances 0.000 description 1
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- 238000010586 diagram Methods 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
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- 229910052719 titanium Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、自動車及び車輌等の各種構造材等として使用される鋼材とアルミニウム系（アルミニウム又はアルミニウム合金）材との複合構造体を得るための異材の抵抗スポット溶接方法に関する。 The present invention relates to a method for resistance spot welding of dissimilar materials to obtain a composite structure of a steel material and an aluminum-based (aluminum or aluminum alloy) material used as various structural materials for automobiles and vehicles.
アルミニウム又はアルミニウム合金（以下、総称してアルミニウム系という）材は、軽量な構造材料として、自動車及び車輌等に使用されている。この場合に、コスト、強度及び車体剛性等の種々の要因から、アルミニウム系材は、鋼材と組み合わせた複合材として使用されることが多い。このためには、アルミニウム系材と鋼材とを接合する必要がある。 Aluminum or aluminum alloy (hereinafter collectively referred to as aluminum-based) materials are used in automobiles and vehicles as lightweight structural materials. In this case, the aluminum-based material is often used as a composite material combined with a steel material due to various factors such as cost, strength, and vehicle body rigidity. For this purpose, it is necessary to join an aluminum-based material and a steel material.
鋼材同士の場合は、その簡便な接合方法として、抵抗スポット溶接方法が広く使用されている。そこで、アルミニウム系材と鋼材との接合にも、抵抗スポット溶接の適用が要望されている。この異種材料（以下、異材という）の抵抗スポット溶接方法として、特許文献１には、鋼材にコーティング層を設けることにより、鋼材とアルミニウム系材との間の溶接部の強度を高めた技術が開示されている。
In the case of steel materials, a resistance spot welding method is widely used as a simple joining method. Therefore, application of resistance spot welding is also demanded for joining aluminum-based materials and steel materials. As a resistance spot welding method for this dissimilar material (hereinafter referred to as a dissimilar material),
しかしながら、アルミニウム系材と鋼材との異材の抵抗スポット溶接方法においては、同種材料のスポット溶接とは異なり、異種の材料の溶融形態が相互に異なるために、溶接条件の適正化が重要である。つまり、図４に示すように、鋼材１及び鋼材２を抵抗スポット溶接する場合は、両者間に適正なナゲット３が形成される。しかし、図５に示すように、鋼材５とアルミニウム系材６との間の抵抗スポット溶接においては、特に、プレス成形後の油剤９がアルミニウム系材６の表面に残存し、被接合材間に油剤９が存在する場合においては、油剤の残留（巻込み）１０が発生する。このように、油剤の残留１０があると、アルミニウム系材６側にチリが発生し、肉厚の減少７が発生する。特に、異材接合においては、アルミニウム系材が過剰に加熱されることによりチリとなって滅失していまい、アルミニウム系材の肉厚が大幅に減少することにより、接合強度が低下してしまうという問題点があった。
However, in the resistance spot welding method of different materials of aluminum-based material and steel material, different from the spot welding of the same kind of material, since the melting forms of different materials are different from each other, it is important to optimize the welding conditions. That is, as shown in FIG. 4, when the
一方、被接合材を洗浄して油分などを除去することも可能であるが、この場合は洗浄工程が増えるため、異材複合構造材の製造工程が複雑になる。従って、異材を洗浄しないまま接合できる抵抗スポット溶接方法が要望されている。 On the other hand, it is possible to clean the material to be joined to remove oil and the like, but in this case, the number of cleaning steps increases, which complicates the manufacturing process of the dissimilar composite structure material. Therefore, there is a demand for a resistance spot welding method capable of joining different materials without cleaning them.
本発明はかかる問題点に鑑みてなされたものであって、鋼材とアルミニウム系材との異材同士を、チリの発生による肉厚の減少なしに高接合強度で接合することができ、破断エネルギが高い強固な接合部を高効率で得ることができる異種材の抵抗スポット溶接方法を提供することを目的とする。 The present invention has been made in view of such problems, and can dissimilar materials of steel and aluminum-based materials can be joined with high joint strength without a reduction in wall thickness due to generation of dust. It is an object of the present invention to provide a resistance spot welding method for dissimilar materials capable of obtaining a high and strong joint with high efficiency.
本発明に係る異材の抵抗スポット溶接方法は、鋼材とアルミニウム又はアルミニウム合金材とを抵抗スポット溶接する異材の抵抗スポット溶接方法において、電極間に電流をパルス状に通電することを特徴とする。この場合に、パルス状に電流を通電するということは、矩形波又は三角波等の形状のパルス波の電流を繰り返し通電することであり、パルス波間の期間には、電流が０の場合と、低い電流が流れる場合とがある。 The different material resistance spot welding method according to the present invention is a different material resistance spot welding method in which a steel material and aluminum or an aluminum alloy material are resistance spot welded, wherein a current is pulsed between electrodes. In this case, energizing the current in a pulse form means repeatedly energizing a pulse wave current having a shape such as a rectangular wave or a triangular wave, and during the period between the pulse waves, the current is as low as 0. In some cases, current flows.
この異材の抵抗スポット溶接方法において、例えば、前記鋼材は、亜鉛又は亜鉛合金が被覆された被覆鋼板である。又は、例えば、前記鋼材は、アルミニウム又はアルミニウム合金がめっきされためっき鋼板である。この場合に、前記めっきは、Ｓｉ：３〜１５質量％、Ｆｅ：０．５〜５質量％を含む溶融アルミニウム合金めっきであることが好ましい。 In this dissimilar resistance spot welding method, for example, the steel material is a coated steel plate coated with zinc or a zinc alloy. Alternatively, for example, the steel material is a plated steel plate plated with aluminum or an aluminum alloy. In this case, the plating is preferably a molten aluminum alloy plating containing Si: 3 to 15% by mass and Fe: 0.5 to 5% by mass.
そして、前記溶接方法に用いる溶接電源はインバーター式であり、電極間に電流をパルス状に通電する際に、通電時間ｔ１が停止時間ｔ２の０．６〜１０倍であり、かつ、ｔ１×パルス数で計算される総通電時間が１２０〜８００ｍｓｅｃであることが好ましい。 And the welding power supply used for the said welding method is an inverter type | formula, When supplying an electric current between electrodes in a pulse form, energization time t1 is 0.6 to 10 times the stop time t2, and t1 * pulse The total energization time calculated by the number is preferably 120 to 800 msec.
また、前記電極間に電流をパルス状に通電する際に、単相交流式電源を使用する場合も、電極間に電流をパルス状に通電する際に、通電時間ｔ１が停止時間ｔ２の０．６〜１０倍であることが好ましい。 Further, even when a single-phase AC power supply is used when applying current between the electrodes in a pulsed manner, when the current is applied in a pulsed manner between the electrodes, the energizing time t1 is 0. It is preferably 6 to 10 times.
本発明者は、異材の抵抗スポット溶接におけるアルミニウム系材のチリ発生について、種々実験研究を繰り返した結果、このチリ発生の原因が、油分等の介在物が鋼材とアルミニウム系材との間に存在することによって、両被接合材間の界面の接合部位における電流密度が過剰になり、融点が低いアルミニウム系材側が過剰に溶融し、滅失してしまうためであることを知見した。そこで、本発明においては、抵抗スポット溶接の通電に際し、電流をパルス状に通電することによって、通電電流を適度に抑制し、アルミニウムのチリの発生を防止する。これにより、アルミニウム系材の肉厚の滅失が防止され、高い継手強度の継手が得られる。 As a result of repeating various experimental studies on the generation of dust in aluminum-based materials in resistance spot welding of dissimilar materials, the present inventor found that the cause of this dust generation is that inclusions such as oil exist between the steel material and the aluminum-based material. As a result, it was found that the current density at the bonding portion at the interface between the two bonded materials becomes excessive, and the aluminum-based material side having a low melting point is excessively melted and lost. Therefore, in the present invention, when the resistance spot welding is energized, by energizing the current in a pulsed manner, the energized current is moderately suppressed and the generation of aluminum dust is prevented. Thereby, the loss of the thickness of the aluminum-based material is prevented, and a joint with high joint strength is obtained.
本発明によれば、抵抗スポット溶接における通電電流を、パルス状としたので、各通電期間の間に、電流が低いか、又は全く流れない期間が存在する。このため、接合界面温度が適度のものとなり、アルミニウム系材のチリ発生が防止される。その結果、アルミニウム系の減肉もなく、高強度の接合部を得ることができる。 According to the present invention, since the energization current in resistance spot welding is pulsed, there is a period in which the current is low or does not flow at all during each energization period. For this reason, the bonding interface temperature becomes moderate, and generation of dust in the aluminum-based material is prevented. As a result, a high-strength joint can be obtained without any aluminum-based thinning.
以下、本発明の実施の形態について添付の図面を参照して具体的に説明する。図１は、本発明の実施形態に係る異材の抵抗スポット溶接方法を示す縦断面図、図２はその通電電流の波形図である。板状の鋼材１３とアルミニウム系材１４とを重ね、電極１１及び電極１２により、鋼材１３とアルミニウム系材１４とを接合する部分を挟持する。そして、電極１１，１２間に図２に示すような波形の電流を通電する。これにより、電流が流れた部分が抵抗発熱し、その部分でスポット溶接される。
Hereinafter, embodiments of the present invention will be specifically described with reference to the accompanying drawings. FIG. 1 is a longitudinal sectional view showing a resistance spot welding method for dissimilar materials according to an embodiment of the present invention, and FIG. 2 is a waveform diagram of the energization current. The plate-
この場合に、本発明においては、図２（ａ）乃至（ｃ）に示すように、通電電流の波形が、断続的なもの、つまりパルス状になるようにする。即ち、通電期間と停止期間とが交互に現れ、通電期間の時間（通電時間）がｔ１、停止期間の時間（停止時間）がｔ２である。図２(ａ)において、通電期間は正の電流と負の電流とが交互に現れるものである。図２（ａ）は、単相交流式電源を用いた場合の波形であり、交流波の１／２サイクル（時間ｔ１＋ｔ２）の内に一定の停止時間ｔ２をおいたものである。図２（ｂ）は、インバーター式電源を用いた場合の波形であり、時間がｔ１の正の矩形波電流を、それらの間にｔ２の停止時間をおいて、断続的に通電したものである。図２（ｃ）は、最大電流でフラットな部分を有し、上昇及び下降時に徐々に立ち上がり又は立ち下がる波形のパルス状の電流を通電したものである。なお、図３は従来の通電電流の波形を示し、所謂正弦波形であり、停止期間が存在しない。停止期間とは、一瞬電流が０になることではなく、電流０の時間が有限に存在するものである。 In this case, in the present invention, as shown in FIGS. 2A to 2C, the waveform of the energization current is made to be intermittent, that is, pulsed. That is, the energization period and the stop period appear alternately, the time of the energization period (energization time) is t1, and the time of the stop period (stop time) is t2. In FIG. 2A, a positive current and a negative current appear alternately during the energization period. FIG. 2 (a) shows a waveform when a single-phase AC power source is used, in which a fixed stop time t2 is placed within a half cycle (time t1 + t2) of the AC wave. FIG. 2 (b) shows a waveform when an inverter type power supply is used, in which a positive rectangular wave current of time t1 is intermittently energized with a stop time of t2 between them. . FIG. 2C shows a case where a pulse-shaped current having a flat portion with a maximum current and having a waveform that gradually rises or falls as it rises and falls is energized. FIG. 3 shows a waveform of a conventional energization current, which is a so-called sine waveform, and there is no stop period. The stop period does not mean that the current becomes zero for a moment, but has a finite time of current zero.
なお、図２（ｂ）又は（ｃ）に示すようなインバーター式電源による矩形波では、通電時間の間には、全く電流が流れないことが好ましいが、電流値が０〜６ｋＡ程度の低い電流が流れていても構わない。 In addition, in the rectangular wave by the inverter type power source as shown in FIG. 2 (b) or (c), it is preferable that no current flows during the energization time, but the current value is a low current of about 0-6 kA. May flow.
本発明においては、上述のように、各通電期間の間に、通電停止期間（状態）を入れることにより、電流が適度に抑えられるため、アルミニウム系材の滅失が起こらない。この場合に、通電時間ｔ１は停止時間ｔ２の０．６〜１０倍であることが好ましい。通電時間／通電停止時間ｔ１／ｔ２が０．６よりも小さい場合は、通電に対して停止時間が長すぎるため電流が不十分となり、良好な溶融状態が得られない。一方、ｔ１／ｔ２が１０を超えると、通電時間が長すぎるため、アルミニウム系材料が過剰に加熱され、チリとなって滅失してしまい、ＣＴＳ、ＴＳＳなどの強度が著しく低くなる。 In the present invention, as described above, since an electric current is moderately suppressed by inserting an energization stop period (state) between the energization periods, the aluminum-based material is not lost. In this case, the energization time t1 is preferably 0.6 to 10 times the stop time t2. When energization time / energization stop time t1 / t2 is smaller than 0.6, the current is insufficient because the stop time is too long for energization, and a good molten state cannot be obtained. On the other hand, when t1 / t2 exceeds 10, since the energization time is too long, the aluminum-based material is excessively heated and lost as dust, and the strength of CTS, TSS, etc. is significantly reduced.
更に、鋼材１３はアルミニウム又はアルミニウム合金をめっきしためっき鋼板であると、アルミニウム系材１４と同種の金属が鋼材１３の表面に被覆されていることになるため、アルミニウム系材１４と鋼材１３との間の親和性が高くなり、より強度が高い接合体が得られる。
Furthermore, if the
ところで、被接合材である溶融アルミニウムめっき鋼板のめっき層組成が接合界面のＡｌ−Ｆｅ二元合金層の生成に大きな影響を及ぼす。即ち、Ｓｉ：３〜１５質量％、Ｆｅ：０．５〜５質量％を含む溶融アルミニウムめっき層が形成されている溶融アルミニウムめっき鋼板をアルミニウム材料と抵抗スポット溶接で接合する場合、合金層消失域のある接合界面が形成され、接合強度が向上する。ここでいうＳｉ、Ｆｅの含有量は、下地鋼／溶融アルミニウムめっき層の界面に形成されるＡｌ−Ｆｅ−Ｓｉ三元系合金層を含まない値である。 By the way, the plating layer composition of the hot dip galvanized steel sheet, which is the material to be joined, has a great influence on the formation of the Al—Fe binary alloy layer at the joint interface. That is, in the case where a hot-dip aluminum plated steel sheet on which a hot-dip aluminum plating layer containing Si: 3 to 15 mass% and Fe: 0.5 to 5 mass% is formed is joined to an aluminum material by resistance spot welding, the alloy layer disappearing region A certain bonding interface is formed, and the bonding strength is improved. The contents of Si and Fe here are values that do not include the Al—Fe—Si ternary alloy layer formed at the interface of the base steel / hot-dip aluminum plating layer.
鋼材１３表面の溶融アルミニウムめっき層のＳｉ，Ｆｅ濃度がＡｌ−Ｆｅ二元合金層の生成に及ぼす影響は、次のように推察される。
The influence of the Si and Fe concentration of the molten aluminum plating layer on the surface of the
Ａｌ−Ｆｅ二元合金層は、スポット溶接時の高温過熱で生成した溶融Ａｌに溶け込んだＦｅが冷却過程で再析出した結果である。溶融Ａｌに対するＦｅの溶け込み量は、下地鋼／めっき層のＦｅの濃度勾配に影響され、濃度勾配が大きいほど、換言すれば、めっき層のＦｅ濃度が低いほど多くなる。溶出したＦｅは、拡散係数が比較的小さいことから下地鋼の近傍に存在し、冷却過程で多量のＡｌ−Ｆｅ二元合金層となって接合界面に再析出する。そこで、めっき層のＦｅ濃度を予め高くしておくと、下地鋼５からめっき層に溶け込むＦｅが少なくなり、結果としてＡｌ−Ｆｅ二元合金層の生成が抑えられる。
The Al—Fe binary alloy layer is a result of reprecipitation of Fe dissolved in molten Al generated by high temperature overheating during spot welding during the cooling process. The amount of Fe penetration into the molten Al is affected by the Fe concentration gradient of the base steel / plating layer, and increases as the concentration gradient increases, in other words, as the Fe concentration in the plating layer decreases. The eluted Fe exists in the vicinity of the base steel because of its relatively small diffusion coefficient, and reprecipitates at the joint interface as a large amount of Al—Fe binary alloy layer during the cooling process. Therefore, if the Fe concentration of the plating layer is increased in advance, Fe that dissolves into the plating layer from the
めっき層のＦｅ濃度が０．５質量％以上になると、電極の中心部ではＡｌ−Ｆｅ２元合金層が生成するものの、中心部に比較して投入熱量の少ない電極の周辺部ではＦｅの溶け込みが抑えられ、合金層消失域が形成される。しかし、Ｆｅ濃度が５質量％を超えると、接合強度向上効果が得られない。 When the Fe concentration in the plating layer is 0.5% by mass or more, an Al—Fe binary alloy layer is formed at the center of the electrode, but Fe permeates at the periphery of the electrode with less input heat than the center. The alloy layer disappearing region is formed. However, if the Fe concentration exceeds 5% by mass, the effect of improving the bonding strength cannot be obtained.
めっき層に含まれるＳｉは、Ｆｅに比較して拡散係数が大きく、スポット溶接時の高温過熱でｌ−Ｆｅ−Ｓｉ三元合金層から溶融Ａｌに容易に移行し、めっき層の全体に分散される。そこで、めっき層のＳｉ濃度を３〜１５質量％と高めに設定することにより、Ａｌ−Ｆｅ−Ｓｉ三元合金層から溶融ＡｌへのＳｉ拡散を遅延させ、接合界面を除く箇所で下地鋼に対するめっき層の密着性を確保する。また、Ｓｉ濃度の増加に応じてＡｌ−Ｆｅ二元合金層が減少する傾向がみられ、結果として接合強度も向上する。なお、めっき層中のＳｉ濃度は１５％を超えると、めっき浴浸漬後の凝固過程で粗大なＳｉが析出するため、めっき層自体の加工性が低下し、加工部材への適用が困難になる。このため、めっき層中のＳｉは１５質量％以下とする。また、めっき鋼板自体の加工性には、めっき層厚さも大きく影響し、膜厚：５〜８０μｍの範囲とすることが好ましい。その他、Ａｌ−Ｆｅの相互拡散反応に大きな影響を及ぼさないＴｉ、Ｓｒ、Ｂ、Ｃｒ、Ｍｎ、Ｚｎ等の元素は、スポット溶接以外の特性向上が必要な場合に、適宜含有することができる。 Si contained in the plating layer has a larger diffusion coefficient than Fe, and easily migrates from the l-Fe-Si ternary alloy layer to molten Al due to high temperature overheating during spot welding, and is dispersed throughout the plating layer. The Therefore, by setting the Si concentration of the plating layer as high as 3 to 15% by mass, the Si diffusion from the Al—Fe—Si ternary alloy layer to the molten Al is delayed, and the base steel is removed from the portion except the bonding interface. Ensure adhesion of plating layer. Further, there is a tendency that the Al—Fe binary alloy layer decreases as the Si concentration increases, and as a result, the bonding strength is also improved. If the Si concentration in the plating layer exceeds 15%, coarse Si is precipitated in the solidification process after immersion in the plating bath, so that the workability of the plating layer itself is lowered and it is difficult to apply it to a processed member. . For this reason, Si in a plating layer shall be 15 mass% or less. In addition, the thickness of the plating layer greatly affects the workability of the plated steel sheet itself, and the film thickness is preferably in the range of 5 to 80 μm. In addition, elements such as Ti, Sr, B, Cr, Mn, and Zn that do not greatly affect the Al—Fe interdiffusion reaction can be appropriately contained when it is necessary to improve properties other than spot welding.
下地鋼から溶融ＡｌへのＦｅ拡散は、下地鋼／めっき層界面にＦｅ拡散防止層を形成することによっても抑えられる。Ｆｅ拡散防止層としては、本願出願人が開発したブレージング用アルミニウムめっき鋼板におけるＮ濃縮層が有効である。Ｎ濃縮層によって下地鋼から溶融Ａｌに溶けこむＦｅが少なくなるので、接合界面に生成する脆弱なＡｌ−Ｆｅ二元合金層がいっそう減少し、接合強度の高い接合構造体が得られる。 Fe diffusion from the base steel to the molten Al can also be suppressed by forming an Fe diffusion prevention layer at the base steel / plated layer interface. As the Fe diffusion preventing layer, an N enriched layer in an aluminized steel sheet for brazing developed by the present applicant is effective. Since the Fe enriched in the molten Al from the base steel is reduced by the N enriched layer, the fragile Al—Fe binary alloy layer generated at the joint interface is further reduced, and a joint structure having a high joint strength is obtained.
Ｎ：０．００２〜０．０２０質量％を含む鋼板めっき原板として、溶融アルミニウムめっきした後、特定条件下で加熱処理すると、溶融めっき時に生成した合金層と下地鋼との界面にＮ濃縮層が生成する。この濃縮層の存在によって、Ａｌ−Ｆｅの相互拡散が著しく抑制され、鋼／アルミニウムの接合構造体として好適な溶融アルミニウムめっき鋼板が得られる。Ａｌ−Ｆｅの相互拡散抑制作用は、Ｎ濃縮層のＮ濃度が高いほどＡｌ−Ｆｅの拡散抑制作用が得られるので、濃縮層のＮ濃度が３．０原子量％以上であることが好ましい。また、溶融めっき後の熱処理条件が一定の場合、下地鋼のＮ含有量が多くなるほどＡｌ−Ｆｅの相互拡散抑制作用は向上する。しかし、０．０２質量％を超える過剰量のＮを含む場合、めっき鋼板自体の製造製が低下する。 N: As a steel plate plating original plate containing 0.002 to 0.020 mass%, after hot-dip aluminum plating, when heat-treated under specific conditions, an N-concentrated layer is formed at the interface between the alloy layer generated during hot-dip plating and the base steel. Generate. Due to the presence of this concentrated layer, interdiffusion of Al—Fe is remarkably suppressed, and a hot-dip aluminized steel sheet suitable as a steel / aluminum bonded structure can be obtained. Since the Al—Fe interdiffusion suppression effect is higher when the N concentration of the N concentrated layer is higher, the N—Fe concentration suppressing effect is preferably 3.0 atomic% or more. In addition, when the heat treatment conditions after hot dipping are constant, the Al—Fe interdiffusion suppression action improves as the N content of the base steel increases. However, when an excessive amount of N exceeding 0.02% by mass is included, the production of the plated steel sheet itself decreases.
鋼材に亜鉛又は亜鉛合金を被覆しためっき鋼板を、アルミニウム又はアルミニウム合金とのスポット溶接接合体に用いた場合、通常のスポット溶接では良好な強度が得られない。しかし、本発明のパルス制御によってスポット溶接時の温度が高温まで上昇しない適切な条件を選定すれば、亜鉛又は亜鉛合金めっき層自体の融点がアルミニウム合金より低いことから、良好な接合強度を示す接合構造体を得ることが可能になる。 When a plated steel sheet in which a steel material is coated with zinc or a zinc alloy is used for a spot welded joint with aluminum or an aluminum alloy, good strength cannot be obtained by ordinary spot welding. However, if an appropriate condition is selected so that the temperature during spot welding does not increase to a high temperature by the pulse control of the present invention, the melting point of the zinc or zinc alloy plating layer itself is lower than that of the aluminum alloy. A structure can be obtained.
次に、本発明の実施例について説明して、本発明の効果を説明する。下記表１に示す厚さ１．０ｍｍのアルミニウムメッキ鋼板と厚さ１．０ｍｍのＪＩＳ６０６１Ａｌ合金板とを、いずれの板も防錆油が付着したまま使用し、溶接加圧力を２．９ｋＮとして、通電電流及び通電時間を下記表１に記載のように制御しながら、抵抗スポット溶接により接合し、異種接合体を得た。これらの溶接条件で接合した試験片における十字引張強度（ＣＴＳ）および引張剪断試験（ＴＳＳ）により破断した試験片における被溶接部の破断形態を表２に示す。また、得られた継手から図に示す引張試験片を加工し、引張剪断強度を求めた結果を表２に示す。 Next, examples of the present invention will be described to explain the effects of the present invention. A 1.0 mm thick aluminum-plated steel sheet and a 1.0 mm thick JIS6061Al alloy plate shown in Table 1 below are used with rust preventive oil attached to each plate, and the welding pressure is 2.9 kN. While controlling the energization current and the energization time as described in Table 1 below, joining was performed by resistance spot welding to obtain a heterogeneous joined body. Table 2 shows the fracture forms of the welded parts in the test pieces fractured by the cross tensile strength (CTS) and the tensile shear test (TSS) in the test pieces joined under these welding conditions. In addition, Table 2 shows the results obtained by processing the tensile test pieces shown in the figure from the obtained joints and obtaining the tensile shear strength.
この表１及び表２から明らかなように、実施例１乃至６はｔ１／ｔ２が０．６乃至１０であるので、接合強度が十分に高いと共に、アルミニウムのチリ飛散も少ないものであった。これに対し、比較例１は、ｔ１／ｔ２が０．６より小さく、溶融径（ナゲット）が小さく、十分な接合強度が得られなかった。比較例２はｔ１×Ｐが１０５であるので溶融径（ナゲット）が小さく、十分な接合強度が得られなかった。比較例３，４はｔ１／ｔ２が１０を超えているので、アルミニウムのチリが多量であり、接合強度が低いものであった。比較例５はｔ１×Ｐが８００と高く、アルミニウムのチリが多量であり、接合強度が低いものであり、比較例６はパルス間電流／溶接電流が７７％と高く、同様に、アルミニウムのチリが多量であり、接合強度が低いものであった。 As is clear from Tables 1 and 2, Examples 1 to 6 had t1 / t2 of 0.6 to 10, so that the bonding strength was sufficiently high and the aluminum dust was not scattered. On the other hand, in Comparative Example 1, t1 / t2 was smaller than 0.6, the melt diameter (nugget) was small, and sufficient bonding strength was not obtained. In Comparative Example 2, since t1 × P was 105, the melt diameter (nugget) was small, and sufficient bonding strength was not obtained. In Comparative Examples 3 and 4, since t1 / t2 exceeded 10, the amount of aluminum dust was large and the bonding strength was low. Comparative Example 5 has a high t1 × P of 800, a large amount of aluminum dust and low joint strength, and Comparative Example 6 has a high pulse current / welding current of 77%. Was a large amount and the bonding strength was low.
実施例２として、Ｃ：０．０５質量％、Ｓｉ：０．１質量％、Ｍｎ：０．２５質量％、Ｐ：０．０１２質量％、Ｓ：０．００６質量％、Ａｌ：０．００６質量％を含み残部Ｆｅからなる冷延鋼板を溶融アルミニウムめっきした。この溶融アルミニウムめっき処理では、溶融アルミニウムめっき層のＳｉ含有量を下記表３に示す値となるように調整し、厚さが２５μｍとなるように調整した。アルミニウム材には、厚さが１．０ｍｍのＪＩＳ６０６１アルミニウム合金板を使用した。 As Example 2, C: 0.05 mass%, Si: 0.1 mass%, Mn: 0.25 mass%, P: 0.012 mass%, S: 0.006 mass%, Al: 0.006 A cold-rolled steel sheet including the remaining part and including the balance Fe was subjected to hot-dip aluminum plating. In this hot-dip aluminum plating treatment, the Si content of the hot-dip aluminum plating layer was adjusted to the value shown in Table 3 below, and the thickness was adjusted to 25 μm. As the aluminum material, a JIS6061 aluminum alloy plate having a thickness of 1.0 mm was used.
これらの被接合材に対し、溶接加圧力を２．９ｋＮとして上記実施例２の溶接条件で抵抗スポット溶接を行った。作成された構造体の接合強度を引張剪断試験及び十字引張試験で測定した。表３の試験結果にみるように、溶融アルミニウムめっき層のＳｉ、Ｆｅ濃度が適正範囲（Ｓｉ：３〜１５質量％、Ｆｅ：０．５〜５質量％）に維持されると、引張剪断強度：２．６ｋＮ以上、十字引張強度１．３ｋＮ以上と高い接合強度を持つ接合構造体が得られることがわかる。 Resistance spot welding was performed on the materials to be joined under the welding conditions of Example 2 above with a welding pressure of 2.9 kN. The joint strength of the prepared structure was measured by a tensile shear test and a cross tensile test. As can be seen from the test results in Table 3, when the Si and Fe concentrations of the molten aluminum plating layer are maintained in appropriate ranges (Si: 3 to 15% by mass, Fe: 0.5 to 5% by mass), the tensile shear strength : It can be seen that a bonded structure having a high bonding strength of 2.6 kN or more and a cross tensile strength of 1.3 kN or more can be obtained.
以上詳述したように、本発明によれば、アルミニウム系材と鋼材が抵抗スポット溶接によって強固に接合され、アルミニウム系材及び鋼材の長所を活かした接合構造体を得ることができ、車輌構造体、熱交換器用など、種々の構造部材に使用することができる。 As described above in detail, according to the present invention, an aluminum-based material and a steel material are firmly joined by resistance spot welding, and a bonded structure that takes advantage of the advantages of the aluminum-based material and the steel material can be obtained. It can be used for various structural members such as for heat exchangers.
１、２、５：鋼材
３：ナゲット
６：アルミニウム系材
９：油剤
１０：油剤の残留（巻込み）
１１，１２：電極
１３：鋼材
１４：アルミニウム系材
1, 2, 5: Steel material 3: Nugget 6: Aluminum-based material 9: Oil agent 10: Residue of oil agent (entrainment)
11, 12: Electrode 13: Steel material 14: Aluminum-based material
Claims (5)
4. The resistance spot welding method for dissimilar materials according to claim 3, wherein the plating is a molten aluminum alloy plating containing Si: 3 to 15% by mass and Fe: 0.5 to 5% by mass.
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