JP4683890B2 - Mg component-containing Zn-based alloy plated steel plate spot welding electrode - Google Patents
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本発明は、Ｍｇ成分を含有するＺｎ系合金めっきを施しためっき鋼板をスポット溶接する際に用いる電極に関する。 The present invention relates to an electrode used when spot-welding a plated steel sheet on which a Zn-based alloy plating containing an Mg component is applied.
従来から、自動車や家電製品等の組立てラインにおいては、抵抗溶接法の中でも作業効率の高いスポット溶接法が多用されている。そして、大量生産ラインでは、連続的にスポット溶接が実施されている。このため、スポット溶接用の電極は、高熱，高負荷を繰り返し受ける状況下にあり変形しやすいので、その素材としては変形に耐え得るものでなければならない。しかも、抵抗溶接用電極の本来の必要条件である、高電気伝導度，高熱伝導性及び高強度，高耐摩耗性を備えていることが要求される。このような背景のもと、スポット溶接用電極としてはＣｕ−Ｃｒ、Ｃｕ−Ｃｒ−Ｚｒ等のＣｕ合金や、Ａｌ2Ｏ3等の硬質物質を分散させたＣｕ材が用いられている。熱伝導特性や強度、コスト等の総合的な観点から、Ｃｕ−Ｃｒ合金が用いられる場合が多い。 2. Description of the Related Art Conventionally, spot welding methods with high work efficiency are frequently used among resistance welding methods in assembly lines for automobiles, home appliances, and the like. In a mass production line, spot welding is continuously performed. For this reason, the electrode for spot welding is subject to repeated high heat and high load, and is easily deformed. Therefore, the material of the electrode must be able to withstand deformation. Moreover, it is required to have high electrical conductivity, high thermal conductivity, high strength, and high wear resistance, which are the essential requirements for resistance welding electrodes. Against this background, Cu alloys in which a Cu alloy such as Cu—Cr or Cu—Cr—Zr or a hard material such as Al 2 O 3 is dispersed are used as the spot welding electrode. Cu-Cr alloys are often used from a comprehensive viewpoint such as heat conduction characteristics, strength, and cost.
また一方で、耐久性向上のために自動車や家電製品等の素材として、ＺｎめっきまたはＺｎ合金めっきが施されためっき鋼板が多く使用されるようになっている。これらのめっき鋼板をスポット溶接する際には、冷延鋼板をスポット溶接する際と比較して、大電流を流すことになるため、電極先端部がさらに過酷な条件下におかれることになる。溶接中の電極先端では、めっき層の成分であるＺｎやＡｌ、或いはめっき鋼板の母材成分であるＦｅと電極の主成分であるＣｕとが合金化反応を起こし、Ｃｕ−ＺｎやＣｕ−Ｚｎ−Ａｌ−Ｆｅ等の金属間化合物を形成してしまう。これらの金属間化合物は非常に脆いため、溶接時の加圧で剥離してしまい、結果として電極先端径が拡大して電流密度が低下することになる。このように、めっき鋼板の溶接では、普通鋼やステンレス鋼などの冷延鋼板を溶接する場合と比較すると、電極寿命が短いという欠点がある。
そこで、電極の高寿命化を狙って、電極本体をＷ−Ｍｏ合金、或いは各種ドープ剤を添加したＷ−Ｍｏ合金材料で構成したものや、電極先端中央部に埋め込んだ材料とその周囲の材料とが異なる二重構造の電極等が提案されている。
On the other hand, in order to improve durability, plated steel sheets on which Zn plating or Zn alloy plating has been applied are often used as materials for automobiles, home appliances, and the like. When spot-welding these plated steel sheets, a larger current flows than when spot-welding cold-rolled steel sheets, so that the electrode tip is placed under more severe conditions. At the electrode tip during welding, Zn or Al, which is a component of the plating layer, or Fe, which is the base material component of the plated steel sheet, and Cu, which is the main component of the electrode, cause an alloying reaction, and Cu—Zn or Cu—Zn. -Intermetallic compounds such as Al-Fe are formed. Since these intermetallic compounds are very brittle, they are peeled off by pressurization during welding, and as a result, the electrode tip diameter is enlarged and the current density is lowered. As described above, the welding of the plated steel sheet has a drawback that the electrode life is short as compared with the case of welding a cold-rolled steel sheet such as plain steel or stainless steel.
Therefore, with the aim of extending the life of the electrode, the electrode body is made of a W-Mo alloy or a W-Mo alloy material with various dopants added, and the material embedded in the center of the electrode tip and the surrounding material A double-structured electrode and the like different from the above have been proposed.
Ｗ−Ｍｏ合金材料からなる電極としては、例えば特許文献１に、酸化物，窒化物，金属単体，炭化物，ホウ化物の形態で、Ｋを１０〜１００ｐｐｍ含有させたＷ−Ｍｏ合金を用いたものが、また特許文献２に、酸化物，窒化物，金属単体，炭化物，ホウ化物の形態で、Ｌａ，Ｃｅ，Ｐｒ，Ｎｄ，Ｐｍ，Ｓｍ，Ｅｕ，Ｇｄ，Ｔｂ，Ｄｙ，Ｈｏ，Ｅｒ，Ｔｍ，Ｙｂ，Ｙの希土類元素を１０〜１００ｐｐｍ含有させたＷ−Ｍｏ合金を用いたものが提案されている。
As an electrode made of a W-Mo alloy material, for example, Patent Document 1 uses a W-Mo alloy containing 10 to 100 ppm of K in the form of oxide, nitride, simple metal, carbide or boride. However, in
二重構造の電極としては、例えば、特許文献３に、高強度高導電性のＣｕ合金からなる電極本体の被溶接材に当接する当接面に、その２０〜７０％の面積領域を占めるように、前記被溶接材と合金化し難い、或いは溶着し難い、例えばＡｌ2Ｏ3分散Ｃｕ合金等の金属を埋設したものが提案されている。
また、特許文献４には、高電気伝導材であるＣｕもしくはＣｕ−Ｃｒ合金によって形成された外周部と、セラミックス等の非電気伝導材によって形成された中央部とからなる二重構造のものが提案されている。
さらに、特許文献５には、電極本体が被溶接材に当接する面に、電気伝導度及び熱伝導度に優れ、しかもＣｕ若しくはＣｕ合金からなる電極本体よりも高強度の、例えばＷやＭｏからなる芯材を、当接面の５〜２０％の面積を占めるように埋設したものが提案されている。
さらにまた、特許文献６には、Ｗ，Ｍｏ又はこれらの合金の焼結体からなるチップ主体を、保持リングに嵌着した電極チップを備えたものが提案されている。
Patent Document 4 discloses a double structure composed of an outer peripheral portion formed of Cu or a Cu—Cr alloy, which is a high electrical conductive material, and a central portion formed of a non-electric conductive material such as ceramics. Proposed.
Further, in Patent Document 5, the surface of the electrode body that comes into contact with the material to be welded is excellent in electrical conductivity and thermal conductivity, and has higher strength than the electrode body made of Cu or Cu alloy, for example, from W or Mo. A material in which the core material is embedded so as to occupy an area of 5 to 20% of the contact surface has been proposed.
Furthermore, Patent Document 6 proposes an electrode chip including a chip main body made of a sintered body of W, Mo or an alloy thereof and fitted to a holding ring.
近年、耐食性を高め、耐久性を向上させるために、Ｚｎ系めっき鋼板として、Ｍｇ成分を含むＺｎ−Ａｌ−Ｍｇ系合金めっきを施したものが多用されるようになった。
Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板のスポット溶接を行う際、特許文献１，２で提案されたようなＷやＭｏからなる電極や、ＷとＭｏとの合金材料からなる電極を用いても、めっき金属との合金化反応を比較的抑制でき、効率良く溶接できる。
しかしながら、電極寿命を極力延ばしたいという願望のもとでは、ＷやＭｏ、或いはＷ−Ｍｏ合金材料で構成した電極でも、Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板のスポット溶接を行う際には、必ずしも十分な電極寿命は得られない。
ＷやＭｏ基の金属・合金も、ＣｕないしＣｕ合金と比べるとめっき金属との合金化反応性は低いが、皆無ではない。特にめっき合金中に含まれているＭｇ成分との反応性については検討の余地がある。また、ＷやＭｏ基の金属・合金は硬質であるが故に、加圧時の衝撃でクラックの発生等、破損しやすい欠点も有している。このために、ＷやＭｏからなる電極や、ＷとＭｏとの合金材料からなる電極の改良の余地があると言える。
In recent years, in order to enhance corrosion resistance and improve durability, a Zn-plated steel sheet that has been subjected to Zn-Al-Mg-based alloy plating containing an Mg component has been frequently used.
When performing spot welding of a Zn—Al—Mg alloy-plated steel sheet, even if an electrode made of W or Mo as proposed in
However, under the desire to extend the electrode life as much as possible, even when an electrode made of W, Mo, or a W—Mo alloy material is used for spot welding of a Zn—Al—Mg alloy plated steel sheet, it is not always necessary. A sufficient electrode life cannot be obtained.
W and Mo-based metals / alloys also have low alloying reactivity with plating metal compared to Cu or Cu alloys, but it is not completely absent. In particular, there is room for studying the reactivity with the Mg component contained in the plating alloy. In addition, since W and Mo-based metals and alloys are hard, they also have drawbacks such as the occurrence of cracks due to impact during pressurization, and the like. For this reason, it can be said that there is room for improvement of an electrode made of W or Mo or an electrode made of an alloy material of W and Mo.
また、特許文献３のように、芯材にもＣｕ合金を用いたものにあっては、めっき金属との合金化は避け難い。また、特許文献５のように、芯材として単にＷやＭｏ基の金属・合金を用いたものにあっても、特許文献１，２で問題になるような点は解消されない。
さらに、特許文献４で提案された電極のように脆いセラミックスを芯材として用いたものは、電極加圧時の割れにより剥離しやすくなり、ナゲット形成が不安定となる。
Further, as in
Further, a material using brittle ceramics as a core material like the electrode proposed in Patent Document 4 is easily peeled off by cracking when the electrode is pressed, and the nugget formation becomes unstable.
さらにまた、特許文献６で提案された電極では、保持リングに、強度と靭性の高い例えば析出硬化型のステンレス鋼が用いられており、保持リング部の電気伝導性が良くない。また、芯材自体の問題点も解消できない。しかも電極そのものの製造コストが高くなっている。
本発明は、このような問題を解消すべく案出されたものであり、Ｍｇ成分を含有するＺｎ合金めっきを施しためっき鋼板を大電流下でスポット溶接にする際にあっても、めっき金属との溶着・合金化を抑え、亀裂の発生を防止して長寿命化を可能としたスポット溶接用電極を安価に提供することを目的とする。
Furthermore, in the electrode proposed in Patent Document 6, for example, precipitation hardening stainless steel having high strength and toughness is used for the retaining ring, and the electrical conductivity of the retaining ring portion is not good. In addition, the problems of the core material itself cannot be solved. In addition, the manufacturing cost of the electrode itself is high.
The present invention has been devised to solve such problems, and even when a plated steel sheet plated with a Zn alloy containing an Mg component is spot welded under a large current, the plated metal It is an object of the present invention to provide an inexpensive spot welding electrode that suppresses welding / alloying and prevents the occurrence of cracks and extends the service life.
本発明のＭｇ成分含有Ｚｎ合金めっき鋼板スポット溶接用電極は、その目的を達成するため、Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれた少なくとも一種以上の微粒子を０．５〜１０体積％の割合で分散させたＷ又はＭｏ若しくはそれらを基材とする合金の焼結体で構成されていることを特徴とする。
Ｃｕ又はＣｕ合金からなる電極本体の被溶接材に当接する当接面に、Ｗ又はＭｏ若しくはそれらを基材とする焼結体からなる芯材を埋設した電極であって、前記芯材が、Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれた少なくとも一種以上の微粒子を０．５〜１０体積％の割合で分散させたＷ又はＭｏ若しくはそれらを基材とする合金の焼結体で構成されていることを特徴とする。
In order to achieve the object, the Mg component-containing Zn alloy-plated steel sheet spot welding electrode of the present invention has at least one kind of fine particles selected from oxides of Be, Mg, Ca, Sr, Ti, Zr, Y, and Ce. It is characterized by being comprised by the sintered compact of W or Mo which disperse | distributed in the ratio of 0.5-10 volume%, or the alloy which uses those as a base material.
An electrode in which a core material made of a sintered body based on W or Mo or a base material thereof is embedded in a contact surface of the electrode main body made of Cu or Cu alloy, which is in contact with the workpiece, and the core material is W or Mo in which at least one kind of fine particles selected from oxides of Be, Mg, Ca, Sr, Ti, Zr, Y, and Ce are dispersed at a ratio of 0.5 to 10% by volume, or a base material thereof. It is characterized by comprising a sintered body of an alloy.
本発明は、Ｗ又はＭｏ若しくはそれらを基材とする合金の焼結体で構成されたスポット溶接用電極にあって、当該Ｗ，Ｍｏ系焼結体として、Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれる少なくとも一種以上の微粒子を０．５〜１０体積％の割合で分散させたものを用いることにより、Ｍｇ成分を含有したＺｎ合金めっき鋼板をスポット溶接しても、めっき金属との溶着・合金化を抑制し、かつ溶接時の加圧による亀裂発生を抑制して、スポット溶接用電極としても寿命を長くすることができる。
上記微粒子を含有するＷ又はＭｏ若しくはそれらを基材とする合金の焼結体を、Ｃｕ又はＣｕ合金からなる電極本体の被溶接材に当接する当接面に芯材を埋設した二重構造電極の、前記芯材材料として用いるときも同様に、めっき金属との溶着・合金化を抑制し、かつ溶接時の加圧による亀裂発生を抑制して、スポット溶接用電極としても寿命を長くすることができる。
このため、最近多用されているＭｇ成分を含有したＺｎ合金めっき鋼板を生産性良くスポット溶接することが可能になる。
The present invention is an electrode for spot welding composed of a sintered body of W or Mo or an alloy based on them, and as the W, Mo-based sintered body , Be, Mg, Ca, Sr, Ti , Zr, Y, Ce, and at least one kind of fine particles dispersed in a proportion of 0.5 to 10% by volume, spot-welded Zn alloy plated steel sheet containing Mg component However, welding and alloying with the plating metal can be suppressed, and cracking due to pressurization during welding can be suppressed, and the life of the electrode for spot welding can be extended.
A double structure electrode in which a sintered body of W or Mo containing the fine particles or an alloy based on them is embedded in a contact surface of the electrode main body made of Cu or Cu alloy in contact with the welded material. Similarly, when used as the core material, the welding and alloying with the plating metal are suppressed, and cracking due to pressurization during welding is suppressed, thereby extending the life of the electrode for spot welding. Can do.
For this reason, it is possible to spot weld a Zn alloy plated steel sheet containing a Mg component that has been frequently used recently with high productivity.
本発明者等は、前述した従来技術の有する欠点を解消するために、Ｍｇ成分を含有したＺｎ合金めっき鋼板をスポット溶接する際に用いる電極の寿命向上策について、材質或いは形状の面から種々の実験・検討を重ねてきた。
本発明者等は、まず、電極素材として用いるＷやＭｏ基の金属・合金の特性の向上策について検討した。Ｗ，Ｍｏ系の金属・合金はＣｕないしＣｕ合金と比べるとめっき金属との反応性は低いが、大気雰囲気下では皆無ではなく、溶着しやすいという欠点がある。また、Ｗ，Ｍｏ系の金属・合金は硬質であるが故に、加圧時の衝撃でクラックの発生等、破損しやすい欠点も有している。
そこで、電極素材として用いるＷ又はＭｏ若しくはそれらを基材とする合金の焼結体も、めっき金属との溶着を抑制し、かつ加圧時のクラック発生を抑制できるように改良したものを用いると寿命が延びることが予測される。
In order to eliminate the above-mentioned drawbacks of the prior art, the present inventors have various methods for improving the life of electrodes used when spot-welding Zn alloy plated steel sheets containing Mg components in terms of material or shape. I have been experimenting and studying.
The present inventors first examined measures for improving the characteristics of W- or Mo-based metals and alloys used as electrode materials. W and Mo-based metals / alloys are less reactive with the plating metal than Cu or Cu alloys, but have the disadvantage that they are not completely present in the atmosphere and are easily welded. In addition, since W and Mo-based metals and alloys are hard, they also have drawbacks such as the occurrence of cracks due to impact during pressurization, and the like.
Therefore, when W or Mo used as an electrode material or a sintered body of an alloy based on them is used to improve welding so as to suppress welding with a plating metal and to suppress generation of cracks during pressurization. Life expectancy is expected to be extended.
ところで、めっき金属にＭｇ成分が含まれているときに電極とめっき金属が溶着しやすい理由として、めっき金属中のＭｇ成分が酸化されやすいために、抵抗溶接中に形成されたＭｇＯが電極先端部に堆積することが挙げられる。電極先端部に堆積したＭｇＯは、電極とめっき鋼板間の抵抗を高くして当該部分の温度を高め、さらにＭｇＯの生成・堆積を助長することになる。そして、電極とめっき鋼板間の抵抗が高くなりすぎると、通電した電流が電極とめっき鋼板間で消費されるために、被溶接材であるめっき鋼板間でのナゲット形成に寄与し難くなり、結果的に良好なスポット溶接部が得難くなる。 By the way, the reason why the electrode and the plated metal are likely to be welded when the plated metal contains the Mg component is that the Mg component in the plated metal is easily oxidized, so the MgO formed during resistance welding is It can be mentioned that it is deposited on. MgO deposited on the tip of the electrode increases the resistance between the electrode and the plated steel sheet to increase the temperature of the part, and further promotes the generation and deposition of MgO. And, if the resistance between the electrode and the plated steel sheet becomes too high, since the energized current is consumed between the electrode and the plated steel sheet, it becomes difficult to contribute to the formation of the nugget between the plated steel sheets that are to be welded. Therefore, it is difficult to obtain a good spot weld.
改良手段としては、電極基材のＷ又はＭｏ若しくはそれらを基材とする合金の焼結体中にＢｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれる少なくとも一種以上の微粒子を０．５〜１０体積％の割合で分散させることが有効であることを確認した。
電極基材に金属酸化物の微粒子を分散させた場合、電極とめっき金属とが反応し難くなり、溶着が起こり難くなると考えられるが、より確実に溶着を抑制するためには、電極に分散させる金属酸化物とめっき層に含まれる金属の双方の物性に着目する必要がある。
As an improvement means, at least one or more selected from oxides of Be, Mg, Ca, Sr, Ti, Zr, Y, and Ce in a sintered body of W or Mo of an electrode substrate or an alloy based on them. It was confirmed that it was effective to disperse the fine particles at a ratio of 0.5 to 10% by volume.
When metal oxide fine particles are dispersed in the electrode base material, it is considered that the electrode and the plating metal are less likely to react with each other and welding is unlikely to occur. However, in order to suppress the welding more reliably, the electrode is dispersed in the electrode. It is necessary to pay attention to the physical properties of both the metal oxide and the metal contained in the plating layer.
上記金属の酸化物は、標準生成自由エネルギーがＭｇＯの標準生成自由エネルギーよりも低いか或いは同等であるので、Ｍｇ成分を含有するＺｎ系合金めっき鋼板をスポット溶接する際、溶融ないし半溶融状態のめっき層中に含まれるＭｇが上記金属酸化物の還元によって酸化することはなくなる。ＭｇＯの生成・堆積が抑制されるので、Ｗ又はＭｏ若しくはそれらを基材とする合金からなる電極とめっき金属との濡れ性を阻害する効果が向上し、めっき金属の溶着をより確実に抑制できることになる。
さらに、Ｗ又はＭｏ若しくはそれらを基材とする合金の焼結体中に分散させた酸化物微粒子は、電極が衝撃を受けた際の転位の伝播をピン止めする作用を発揮し、結果的に耐衝撃性に優れ、クラックの発生等を抑制することができる。さらにまた、これらの酸化物は融点が高いために、ＷやＭｏ中に分散させても焼結体の強度が維持でき、電極の長寿命化には好適である。
The metal oxide has a standard free energy of formation lower than or equal to the standard free energy of MgO, so when spot welding a Zn-based alloy plated steel sheet containing the Mg component, it is in a molten or semi-molten state. Mg contained in the plating layer is not oxidized by the reduction of the metal oxide. Since the production and deposition of MgO are suppressed, the effect of inhibiting the wettability between the electrode made of W or Mo or an alloy based thereon and the plating metal is improved, and the welding of the plating metal can be more reliably suppressed. become.
Furthermore, the oxide fine particles dispersed in the sintered body of W or Mo or an alloy based on them exhibit the effect of pinning the propagation of dislocations when the electrode is impacted, resulting in It is excellent in impact resistance and can suppress the occurrence of cracks. Furthermore, since these oxides have a high melting point, the strength of the sintered body can be maintained even when dispersed in W or Mo, which is suitable for extending the life of the electrode.
上記酸化物微粒子の配合割合は０．５〜１０体積％にすることが好ましい。上記作用を効果的に発揮させるためには０．５体積％以上分散させることが好ましい。また１０体積％を超えて多量に含有させると、Ｗ又はＭｏ若しくはそれらを基材とする合金の焼結体の電気伝導度が低くなりすぎ、抵抗溶接中に電極先端の温度が高くなりすぎて、却って溶着を起こしやすくなる。また、酸化物微粒子を多量に含有させると、焼結体が脆くなり、後述のスエージング加工等、所望形状への加工が困難になる。好ましい配合割合は、０．８〜３体積％である。
また、Ｃｅ2Ｏ3等、含有させる酸化物微粒子の粒径は、０．５〜１０μｍ程度が好ましい。１０μｍを超えるほどに大きな粒子を分散させると、熱膨張率の差によって破壊の起点になりやすい。
The mixing ratio of the oxide fine particles is preferably 0.5 to 10% by volume. In order to effectively exhibit the above action, it is preferable to disperse 0.5% by volume or more. If it is contained in a large amount exceeding 10% by volume , the electrical conductivity of the sintered body of W or Mo or an alloy based on them becomes too low, and the temperature at the electrode tip becomes too high during resistance welding. On the contrary, it becomes easy to cause welding. In addition, when a large amount of oxide fine particles is contained, the sintered body becomes brittle, and processing into a desired shape such as swaging processing described later becomes difficult. A preferable mixing ratio is 0.8 to 3% by volume.
Further, the particle diameter of the oxide fine particles to be contained such as Ce 2 O 3 is preferably about 0.5 to 10 μm. When particles larger than 10 μm are dispersed, it tends to become a starting point of destruction due to a difference in thermal expansion coefficient.
なお、スポット溶接用電極として使用されるＷやＭｏは、それぞれの金属単独で用いられてもよいし、例えば互いに５〜９５質量％の割合の合金として用いられても良いことは言うまでもない。
さらに、電極等に用いられるＷやＭｏの通電焼結体にあっては、１０〜２００ｐｐｍ程度のＫ（カリウム）を、酸化物，窒化物，金属Ｋ，炭化物或いは硼化物の形態でドープされたものが多用されている。本明細書中に記載のＷやＭｏ、或いはＷ−Ｍｏ系合金は上記ドープタングステンをも包含していることも言うまでもない。
In addition, it cannot be overemphasized that W and Mo used as an electrode for spot welding may be used individually by each metal, for example, may be used as an alloy of the ratio of 5-95 mass%, for example.
Furthermore, in the electric current sintered body of W or Mo used for electrodes or the like, about 10 to 200 ppm of K (potassium) is doped in the form of oxide, nitride, metal K, carbide or boride. Things are used a lot. Needless to say, the W, Mo, or W-Mo alloy described in the present specification also includes the doped tungsten.
本発明者等はまた、前記特許文献５で提案されている、Ｃｕ又はＣｕ合金からなる電極本体が被溶接材に当接する面に、電気伝導度及び熱伝導度に優れ高強度のＷやＭｏからなる芯材を埋設した二重構造の電極に着目し、その電極を構成する各材質を種々に変更して、Ｍｇ成分を含有したＺｎ合金めっき鋼板のスポット溶接を実施して、電極寿命を調査した。
その結果、電極本体にＣｕ又はＣｕ合金を用い、芯材に上記Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれる少なくとも一種以上の微粒子を０．５〜１０体積％の割合で分散させたＷ又はＭｏ若しくはそれらを基材とする合金の焼結体を用いた場合、電極自体に当該Ｗ−Ｍｏ系合金の焼結体を用いた場合と同様に、芯材のＭｇ含有めっき金属との耐溶着性を向上させるとともに、溶接時に電極の亀裂発生を抑制し、電極が長寿命化できることを確認した。
The inventors of the present invention have also proposed W or Mo having excellent electrical conductivity and thermal conductivity on the surface of the electrode body made of Cu or Cu alloy, which is proposed in Patent Document 5, which is in contact with the workpiece. Focusing on the electrode of the double structure in which the core material made of is embedded, various materials constituting the electrode are changed, and spot welding of the Zn alloy-plated steel sheet containing the Mg component is carried out to increase the electrode life. investigated.
As a result, Cu or Cu alloy is used for the electrode body, and 0.5 to 10 volumes of at least one kind of fine particles selected from the oxides of Be, Mg, Ca, Sr, Ti, Zr, Y, and Ce are used for the core material. % W, or Mo or dispersed at a ratio in the case where they were a sintered body of an alloy with the substrate, as in the case of using a sintered body of the W-Mo-based alloy in the electrode itself, core member In addition to improving the welding resistance with the Mg-containing plated metal, it was confirmed that cracking of the electrode was suppressed during welding, and that the electrode could have a long life.
従来から、例えば図１に示すような、芯材３を周囲材２に埋め込んだ二重構造の埋め込み型電極１は電極寿命が長いとされているが、その理由は、溶接打点を重ねても埋め込んだ芯材により一定面積の通電路が確保され、それによって安定したナゲットの形成ができる点にある。そのため、芯材の材質としては、ＷやＭｏのように硬質で、めっき金属と溶着し難いものが好ましいことになっている。
そこで、芯材として、Ｍｇを含むめっき金属に対する耐溶着性に優れる前記酸化物微粉末含有のＷ又はＭｏ若しくはそれらを基材とする合金の焼結体を用い、電極本体である周囲材を純Ｃｕとした電極を使用してスポット溶接するとき、従来の単なるＷ系やＭｏ系合金の焼結体を用いた電極を使用してスポット溶接したときよりも、電極先端部へのＭｇＯの堆積が抑制され、長期間にわたっても安定したスポット溶接部が得られることを確認した。
Conventionally, for example, as shown in FIG. 1, a double-structured embedded electrode 1 in which a
Therefore, as a core material, a sintered body of W or Mo containing the above-mentioned fine oxide powder, which is excellent in resistance to welding to a plated metal containing Mg, or an alloy based on them is used, and a surrounding material as an electrode body is pure. When spot welding is performed using an electrode made of Cu, MgO is deposited on the tip of the electrode more than when spot welding is performed using an electrode using a sintered body of a conventional W-based or Mo-based alloy. It was confirmed that a spot weld that was suppressed and stable over a long period of time was obtained.
上述しているように、芯材であるＷ又はＭｏ若しくはそれらを基材とする合金の焼結体の特性を改良しても、芯材の周囲を取り囲むＣｕ材が、スポット溶接時に被溶接材であるＭｇ成分含有Ｚｎ合金めっき鋼板に当接すると、めっき金属、特に含有ＭｇとＣｕ材との合金化反応が起こって、結果的に電極寿命を短くすることになる。したがって、周囲材であるＣｕ材が被溶接めっき鋼板に直接当接しないような電極先端形状にすることが好ましい。このためには、研削により所定形状のコーナーＲを付した電極にあっては、被溶接材との当接面が全て芯材のＷ又はＭｏ若しくはそれらを基材とする合金の焼結体で占めるように、芯材として、当接面よりも直径の太い棒体を用いることが好ましい。 As described above, even if the characteristics of the sintered body of the core material W or Mo or an alloy based on them are improved, the Cu material surrounding the core material is the material to be welded during spot welding. When contacting with the Mg component-containing Zn alloy-plated steel sheet, an alloying reaction between the plated metal, particularly the contained Mg and the Cu material occurs, and as a result, the electrode life is shortened. Therefore, it is preferable to make the electrode tip shape such that the Cu material as the surrounding material does not directly contact the welded plated steel plate. For this purpose, in an electrode with a corner R having a predetermined shape by grinding, the contact surface with the material to be welded is all W or Mo of the core material or a sintered body of an alloy based on them. In order to occupy, it is preferable to use a rod having a diameter larger than that of the contact surface as the core material.
ただし、図１中、直径ｂで示す芯材の断面積と直径ａで示す当接面の面積との面積比率（芯材／当接面）が３００％を超えるような大きな径の芯材３を用いると、周囲材２による芯材の冷却作用が非常に小さくなり、芯材表面にめっき金属が多く堆積して電極と被溶接材との電気抵抗が高くなりすぎてナゲットが形成しにくくなる。逆に、しかし、当接面の面積の７割を下回るほどに小さい芯材径にすると、めっき金属と接触する周囲材の面積が大きくなり、周囲材とめっき金属との合金化による変形が拡径を起こすまでになり、電極全体としてその先端部形状を変形させることになる。
したがって、芯材／当接面の面積比率として表示したとき、その比率は７０〜３００％程度とすることが好ましい。なお、好ましい範囲は、１００〜２００％である。
However, in FIG. 1, the
Therefore, when expressed as an area ratio of the core material / contact surface, the ratio is preferably about 70 to 300%. In addition, a preferable range is 100 to 200%.
ところで、一般的に、Ｗ又はＭｏ若しくはそれらを基材とする合金は焼結法により製造される。本発明で電極本体或いは二重構造電極の芯材として用いられるＷ又はＭｏ若しくはそれらを基材とする合金も通常通り焼結法で製造される。
上記Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｔｉ，Ｚｒ，Ｙ，Ｃｅの酸化物から選ばれる少なくとも一種以上の微粒子とＷ及び／又はＭｏからなる酸化物粉末を混合し、円柱状にプレス成形した後、還元雰囲気で通電焼結を行う。その後、得られた焼結体にスエージング加工やセンターレス研磨等を施して所望の径の棒体を得た後、適当に切断する。原料として、酸化物粉末に代えて金属Ｗ及び／又は金属Ｍｏの粉末を用い、酸化物微粒子を加えてそのまま成形してもよい。
得られた丸棒状焼結体の先端に研削加工を施して、Ｒ形，ＤＲ形，ＣＦ形等、所望の先端部形状に整える。
By the way, generally W or Mo or an alloy based on them is manufactured by a sintering method. In the present invention, W or Mo used as the core material of the electrode body or the double structure electrode or an alloy based on them is also produced by a sintering method as usual.
After mixing at least one kind of fine particles selected from the oxides of Be, Mg, Ca, Sr, Ti, Zr, Y, and Ce and an oxide powder made of W and / or Mo, press-molded into a cylindrical shape, Conduct current sintering in a reducing atmosphere. Thereafter, the obtained sintered body is subjected to swaging processing, centerless polishing, or the like to obtain a rod body having a desired diameter, and then appropriately cut. Instead of the oxide powder, a powder of metal W and / or metal Mo may be used as a raw material, and oxide fine particles may be added and molded as it is.
Grinding is performed on the tip of the obtained round bar-shaped sintered body to prepare a desired tip portion shape such as R shape, DR shape, or CF shape.
二重構造電極の場合、電極本体である周囲材のＣｕ又はＣｕ合金にも、通常のものが使用される。市販の純Ｃｕ、或いはＣｕ−Ｃｒ合金，Ｃｕ−Ｃｒ−Ｚｒ合金等が使用される。さらには、Ａｌ2Ｏ3等の微粒子を分散させた分散強化Ｃｕ合金でも良い。
芯材をＣｕ材からなる周囲材に埋め込む態様も、従来法をそのまま適用できる。穿った孔に芯材を圧入しても良いし、ロウ材を介して挿し込んでも良い。或いは焼き嵌めを行なっても良いし、芯材をＣｕ材で鋳包んだ後冷間鍛造を施しても良い。芯材と周囲材が密に接合されていれば、電気伝導，熱伝導の点で問題になることはない。
二重構造の電極構造体を形成した後、先端に研削加工を施して、Ｒ形，ＤＲ形，ＣＦ形等、所望の先端部形状に整える。
In the case of a dual structure electrode, a normal one is also used as the surrounding material Cu or Cu alloy as the electrode body. Commercially available pure Cu, Cu—Cr alloy, Cu—Cr—Zr alloy or the like is used. Furthermore, a dispersion strengthened Cu alloy in which fine particles such as Al 2 O 3 are dispersed may be used.
The conventional method can be applied as it is to the embodiment in which the core material is embedded in the surrounding material made of the Cu material. A core material may be press-fitted into the bored hole, or may be inserted through a brazing material. Alternatively, shrink fitting may be performed, or cold forging may be performed after casting the core material with a Cu material. If the core material and the surrounding material are closely joined, there is no problem in terms of electrical conduction and heat conduction.
After forming the double-structured electrode structure, the tip is ground and adjusted to a desired tip shape such as an R shape, DR shape, or CF shape.
実施例１：
Ｚｎ−６％Ａｌ−３％Ｍｇ合金めっきを片面当り３０ｇ／ｍ2で施した板厚０．７ｍｍの２枚のＺｎ−Ａｌ−Ｍｇめっき鋼板を、先端直径が６ｍｍ，全体直径が１６ｍｍのＤＲ型で、先端直径６ｍｍの部分に曲率半径４０ｍｍの円弧と他の部分に曲率半径８ｍｍの円弧を付与した電極であって、純度９９．９５％のＷ粉末に種々の配合割合で粒径０．５μｍのＣｅ2Ｏ3粉末を分散させた混合粉末を仮成形後、通電焼結した後にスエージング加工とセンターレス研磨を行ったＷ材からなる電極を上下に用い、表１に示す条件で連続打点の溶接を行った。そして、形成されたナゲット径を測定し、ナゲット径が４√ｔ＝３．３５（ｔは板厚）を下回るものを溶接不良として、電極寿命を求めた。
その結果を表２に示す。
Example 1:
Two Zn-Al-Mg plated steel sheets with a thickness of 0.7 mm, plated with Zn-6% Al-3% Mg alloy at 30 g / m 2 per side, DR with a tip diameter of 6 mm and an overall diameter of 16 mm This is an electrode in which an arc having a radius of curvature of 40 mm is applied to a portion having a tip diameter of 6 mm and an arc having a radius of curvature of 8 mm to the other portion. A mixture powder in which 5 μm of Ce 2 O 3 powder is dispersed is temporarily molded, then subjected to continuous sintering under the conditions shown in Table 1, using electrodes made of W material subjected to swaging and centerless polishing after electric sintering. Spot welding was performed. Then, the formed nugget diameter was measured, and the electrode life was determined by assuming that the nugget diameter was less than 4√t = 3.35 (t is the plate thickness) as poor welding.
The results are shown in Table 2.
表２に示す結果からもわかるように、Ｗ材にＣｅ2Ｏ3の微粒子を０．５〜１０体積％の割合で分散させた電極を用いた場合、比較的に長い電極寿命を得ることができている。また電極断面を観察してもＭｇＯの堆積が非常に少ない状態であった。Ｗ材中に分散させたＣｅ2Ｏ3の微粒子がめっき金属との濡れを抑制したためと考えられる。
一方、微粒子を１１体積％の割合で分散させたＷ材の場合には、電極寿命が低下し、電極断面を観察するとＭｇＯが比較的多く堆積している状態であった。Ｗ材に分散させた微粒子の割合が大きすぎたために、Ｗ材自身の電気抵抗が上昇して電極とめっき鋼板間の発熱量が多くなり、微粒子分散による濡れ抑制作用が低減したためと考えられる。
また微粒子の分散割合が０．２体積％のＷ材の場合にも、電極寿命が比較的短く、電極断面を観察するとＭｇＯが比較的多く堆積している状態であった。Ｗ材に分散させた微粒子が少ないために、濡れ抑制作用を発揮できずに電極とめっき金属が濡れやすかったためと考えられる。
As can be seen from the results shown in Table 2, when an electrode in which Ce 2 O 3 fine particles are dispersed in a W material at a ratio of 0.5 to 10% by volume is used, a relatively long electrode life can be obtained. is made of. Further, even when the electrode cross section was observed, the MgO deposition was very small. This is presumably because the Ce 2 O 3 fine particles dispersed in the W material suppressed wetting with the plated metal.
On the other hand, in the case of the W material in which fine particles are dispersed at a ratio of 11% by volume, the electrode life is reduced, and when the electrode cross section is observed, a relatively large amount of MgO is deposited. It is considered that because the proportion of the fine particles dispersed in the W material was too large, the electrical resistance of the W material itself increased, the amount of heat generated between the electrode and the plated steel plate increased, and the wetting suppression effect due to the fine particle dispersion was reduced.
In the case of a W material having a fine particle dispersion ratio of 0.2% by volume, the electrode life was relatively short, and when the electrode cross section was observed, a relatively large amount of MgO was deposited. This is considered to be because the electrode and the plated metal were easily wetted because the wettability was not exhibited because the fine particles dispersed in the W material were small.
Ｗ材にＣｅ2Ｏ3の微粒子を０．５〜１０体積％の割合で分散させた電極では、ＭｇＯの堆積が比較的少なく、ＭｇＯによる電極とめっき鋼板との間の抵抗の上昇を抑制することができるために、めっき金属との溶着が発生し難い状態であった。
これに対して、Ｃｅ2Ｏ3微粒子の分散割合が多すぎたものや少なすぎたＷ材からなる電極では、ＭｇＯの堆積が比較的多く、このＭｇＯによって電極とめっき鋼板間の抵抗が上昇してめっき金属との溶着が起こりやすい状態であった。また、Ｗ材が一部剥離・脱落していた。
In an electrode in which Ce 2 O 3 fine particles are dispersed in a ratio of 0.5 to 10% by volume in a W material, deposition of MgO is relatively small, and an increase in resistance between the electrode and the plated steel sheet due to MgO is suppressed. Therefore, welding with the plating metal is difficult to occur.
In contrast, in the case of an electrode made of a W material in which the dispersion ratio of Ce 2 O 3 fine particles is too large or too small, MgO is relatively deposited, and this MgO increases the resistance between the electrode and the plated steel sheet. As a result, welding with the plated metal was likely to occur. In addition, the W material was partially peeled off.
実施例２：
Ｗ材に分散させる微粒子として、Ｃｅ2Ｏ3の代わりにＣａＯを用いた以外は実施例１と全く同じ条件で同じめっき鋼板を連続打点溶接し、電極寿命を調査した。
その結果を表３に示す。
Example 2:
The same plated steel sheet was continuously spot welded under exactly the same conditions as in Example 1 except that CaO was used instead of Ce 2 O 3 as fine particles dispersed in the W material, and the electrode life was investigated.
The results are shown in Table 3.
表２，３に示された結果を比較すると、表３の結果、すなわち、Ｃｅ2Ｏ3を分散させたものよりもＣａＯを分散させたものの方が電極寿命は向上している。
Ｃｅ2Ｏ3と比べてＣａＯの方が標準生成自由エネルギーが低いために、めっき金属との濡れ性をより大きく阻害することができ、電極寿命の延びに繋がったものと思われる。また、電極断面を観察すると、ＣａＯを分散させたものの方が電極先端の堆積物は少ない状態であった。
Comparing the results shown in Tables 2 and 3, the electrode life is improved in the results in Table 3, that is, in the case where CaO is dispersed than in the case where Ce 2 O 3 is dispersed.
Since CaO has a lower standard free energy of formation than Ce 2 O 3 , the wettability with the plating metal can be greatly inhibited, which seems to have led to an increase in electrode life. Further, when the electrode cross section was observed, the amount of deposits at the tip of the electrode was smaller in the case where CaO was dispersed.
実施例３：
先端直径が６ｍｍ，全体直径が１６ｍｍのＤＲ型で、先端直径６ｍｍの部分に曲率半径４０ｍｍの円弧と他の部分に曲率半径８ｍｍの円弧を付与した電極であって、芯材として、Ｗ粉末に種々の配合割合で粒径０．５μｍのＣｅ2Ｏ3粉末を分散させた径６ｍｍの焼結・鍛造品を、純Ｃｕからなる周囲材に埋め込んだ電極を上下に用いる点以外は実施例１と全く同じ条件で、同じめっき鋼板を連続打点溶接した。なお、芯材として径６ｍｍの円筒体を用いているので、本実施例では芯材／当接面の面積比率は１００％となっている。
そして、実施例１と同じ評価方法で電極寿命を求めた。
その結果を表４に示す。
Example 3:
It is a DR type with a tip diameter of 6 mm and an overall diameter of 16 mm, an electrode having a tip radius of 6 mm and an arc with a radius of curvature of 40 mm and the other portion with a radius of curvature of 8 mm. Example 1 except that sintered and forged products having a diameter of 6 mm in which Ce 2 O 3 powder having a particle diameter of 0.5 μm is dispersed at various blending ratios and embedded in surrounding materials made of pure Cu are used up and down. The same plated steel sheet was subjected to continuous spot welding under exactly the same conditions. Since a cylindrical body having a diameter of 6 mm is used as the core material, the area ratio of the core material / contact surface is 100% in this embodiment.
And the electrode lifetime was calculated | required with the same evaluation method as Example 1. FIG.
The results are shown in Table 4.
表４に示す結果からもわかるように、一定通電路を確保した二重構造の埋め込み型電極では、Ｃｅ2Ｏ3微粒子の分散量が１１体積％以上になると、分散量が少ないものと比べて寿命に達するまでの打点数が少なくなっている。Ｃｅ2Ｏ3微粒子の分散量が多すぎると芯材の材質が脆くなって、連続打点中に割れが生じ、安定してナゲットが形成し難くなったものと思われる。
Ｃｅ2Ｏ3微粒子の分散量が１１体積％未満のものにあっては１００００打点以上の電極寿命が得られている。Ｃｅ2Ｏ3微粒子の分散量が０．５体積％に満たない電極にあっても、面積比効果によって電極寿命が延びたものと思われる。しかしながら、電極断面を観察してみると、Ｃｅ2Ｏ3微粒子の分散量が０．５体積％に満たない電極では、その先端に、０．５体積％以上のものと比較して比較的多いＭｇＯが堆積していた。このＭｇＯは当然ながらナゲットの形成状況に影響を与える。したがって、正常なナゲットを長期間にわたって安定的に形成するためには、Ｃｅ2Ｏ3微粒子の分散量が０．５〜１０体積％にすることが有効であることがわかる。
As can be seen from the results shown in Table 4, in the double-structured embedded electrode in which a constant current path is ensured, when the dispersion amount of the Ce 2 O 3 fine particles is 11% by volume or more, the dispersion amount is small. The number of hits until the end of the service life is reduced. If the amount of the Ce 2 O 3 fine particles dispersed is too large, the core material becomes brittle, cracks are generated in the continuous hitting points, and it seems that it is difficult to stably form the nugget.
In the case where the dispersion amount of the Ce 2 O 3 fine particles is less than 11% by volume, an electrode lifetime of 10,000 or more is obtained. Even in an electrode in which the dispersion amount of Ce 2 O 3 fine particles is less than 0.5% by volume, it is considered that the electrode life is extended by the area ratio effect. However, when the cross section of the electrode is observed, in the electrode in which the dispersion amount of the Ce 2 O 3 fine particles is less than 0.5% by volume, it is relatively large at the tip of the electrode compared to the one having 0.5% by volume or more. MgO was deposited. This MgO naturally affects the nugget formation status. Therefore, it can be seen that in order to stably form a normal nugget over a long period of time, it is effective to set the dispersion amount of the Ce 2 O 3 fine particles to 0.5 to 10% by volume.
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| US8471169B2 (en) | 2006-06-08 | 2013-06-25 | Nippon Tungsten Co., Ltd. | Electrode for spot welding |
| JP6519510B2 (en) * | 2016-03-28 | 2019-05-29 | マツダ株式会社 | Method of manufacturing spot welds and manufacturing apparatus therefor |
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| JPH02117780A (en) * | 1988-10-27 | 1990-05-02 | Asahi Glass Co Ltd | Electrode covered with ceramic particle dispersed metal and its manufacture |
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| JP2000153371A (en) * | 1998-11-18 | 2000-06-06 | Sumitomo Wiring Syst Ltd | Electrode for resistance welding, resistance welding equipment resistance welding method and production of electrode for resistance welding |
| JP2000158178A (en) * | 1998-11-27 | 2000-06-13 | Sumitomo Wiring Syst Ltd | Method of manufacturing electrode for resistance welding, electrode for resistance welding, and resistance welding equipment |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPS5941838B2 (en) * | 1979-02-15 | 1984-10-09 | 富士重工業株式会社 | Spot welding electrode |
| JPH02117780A (en) * | 1988-10-27 | 1990-05-02 | Asahi Glass Co Ltd | Electrode covered with ceramic particle dispersed metal and its manufacture |
| JPH0324388U (en) * | 1989-07-13 | 1991-03-13 | ||
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| JP2000158178A (en) * | 1998-11-27 | 2000-06-13 | Sumitomo Wiring Syst Ltd | Method of manufacturing electrode for resistance welding, electrode for resistance welding, and resistance welding equipment |
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