JP5099543B2 - Welding method of austempered spheroidal graphite cast iron - Google Patents

Welding method of austempered spheroidal graphite cast iron Download PDF

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JP5099543B2
JP5099543B2 JP2007189347A JP2007189347A JP5099543B2 JP 5099543 B2 JP5099543 B2 JP 5099543B2 JP 2007189347 A JP2007189347 A JP 2007189347A JP 2007189347 A JP2007189347 A JP 2007189347A JP 5099543 B2 JP5099543 B2 JP 5099543B2
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文男 柴田
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本発明は、オーステンパ球状黒鉛鋳鉄の溶接方法に関する。   The present invention relates to a method for welding austempered spheroidal graphite cast iron.

オーステンパ球状黒鉛鋳鉄（以降はＡＤＩと記すこともある）は、球状黒鉛鋳鉄をオーステンパ処理して得られるものである。このＡＤＩは機械的性質が大変優れており鋳鉄の中でも最も高強度であるため、自動車部品や構造部材の材料として有用であり、ＡＤＩの利用によって部材の薄肉化，軽量化が可能である。
特開平１１−１０４８８４号公報 Austempered spheroidal graphite cast iron (hereinafter sometimes referred to as ADI) is obtained by austempering a spheroidal graphite cast iron. This ADI is very excellent in mechanical properties and has the highest strength among cast irons. Therefore, it is useful as a material for automobile parts and structural members, and the use of ADI can reduce the thickness and weight of members.
Japanese Patent Laid-Open No. 11-104884

しかしながら、球状黒鉛鋳鉄の溶接方法は知られているものの（特許文献１を参照）、ＡＤＩを溶接する方法は現在までほとんど研究されておらず、ＡＤＩを欠陥なく溶接する方法は知られていない。すなわち、ＡＤＩは溶接が著しく困難で、ＡＤＩを溶接すると溶接割れ（クラック），気孔（ポロシティ）等の溶接欠陥が生じるため、満足な溶接を行うことができないという難点を有していた。このようなＡＤＩの性質は、ＡＤＩを利用する上で大きな制約となっている。
そこで、本発明は、上記のような従来技術が有する問題点を解決し、溶接割れ，気孔等の溶接欠陥が生じにくいオーステンパ球状黒鉛鋳鉄の溶接方法を提供することを課題とする。 However, although a method for welding spheroidal graphite cast iron is known (see Patent Document 1), a method for welding ADI has hardly been studied until now, and a method for welding ADI without defects is not known. That is, ADI is extremely difficult to weld, and when ADI is welded, welding defects such as weld cracks and porosity occur, so that satisfactory welding cannot be performed. Such a property of ADI is a major limitation in using ADI.
Accordingly, an object of the present invention is to solve the above-described problems of the prior art and to provide a method for welding austempered spheroidal graphite cast iron that is less prone to weld defects such as weld cracks and pores.

前記課題を解決するため、本発明は次のような構成からなる。すなわち、本発明に係る請求項１のオーステンパ球状黒鉛鋳鉄の溶接方法は、少なくとも一方がオーステンパ球状黒鉛鋳鉄からなる２つの部材を突合せ、そこにレーザを照射して前記両部材を溶接するに際して、前記両部材の突合せ面の間にインサート材を挿入してレーザを照射し、前記両部材の突合せ面近傍部分と前記インサート材とを共に溶融、凝固させ前記両部材を溶接するとともに、前記インサート材は、前記両部材の突合せ面近傍部分と前記インサート材とが溶融、凝固した溶融凝固部の組織が、オーステナイト相を主とする組織となるような金属からなり、該金属が、ニッケル及びクロムを合金成分として含有する鋼であることを特徴とする。 In order to solve the above problems, the present invention has the following configuration. That is, in the welding method for austempered spheroidal graphite cast iron according to claim 1 according to the present invention, at least one of the two members made of austempered spheroidal graphite cast iron is abutted, and when the two members are welded by irradiating a laser therewith, Insert material is inserted between the abutting surfaces of both members and irradiated with laser, the abutting surface vicinity portion of both members and the insert material are melted and solidified together, and both the members are welded. the abutting surface near portions of both members and said insert material is melted, solidified melt-solidified portion of the tissue, Ri Do a metal such as a tissue composed mainly of austenite phase, the metal is nickel and chromium characterized Oh Rukoto in steel containing as an alloy component.

また、本発明に係る請求項２のオーステンパ球状黒鉛鋳鉄の溶接方法は、請求項１に記載のオーステンパ球状黒鉛鋳鉄の溶接方法において、前記鋼がＳＵＳ３１０Ｓであることを特徴とする。 Further, the welding method of austempered ductile iron according to claim 2 of the present invention is a method of welding austempered ductile iron according to claim 1, wherein the steel is characterized SUS310S der Rukoto.

本発明のオーステンパ球状黒鉛鋳鉄の溶接方法によれば、溶接割れ等の溶接欠陥をほとんど生じることなくオーステンパ球状黒鉛鋳鉄を溶接することができる。   According to the welding method for austempered spheroidal graphite cast iron of the present invention, austempered spheroidal graphite cast iron can be welded with almost no weld defects such as weld cracks.

本発明に係るオーステンパ球状黒鉛鋳鉄の溶接方法の実施の形態を、図面を参照しながら詳細に説明する。図１，２は、オーステンパ球状黒鉛鋳鉄の溶接方法を説明する図であり、図１は斜視図、図２は一部を破断した側面図である。
板状のＡＤＩ製試験片（縦１００ｍｍ，横１００ｍｍ，厚さ６ｍｍ）を用意して、アセトン中で超音波洗浄した。洗浄した２枚のＡＤＩ製試験片１，１を溶接台１０に載置し、互いの側面１ａ，１ａを突合せた。その際には、突合せた両側面（突合せ面）１ａ，１ａの間に、ニッケル（ただし、不可避の不純物を含有している）製のインサート材３を挿入した。 An embodiment of a welding method for austempered spheroidal graphite cast iron according to the present invention will be described in detail with reference to the drawings. 1 and 2 are views for explaining a welding method for austempered spheroidal graphite cast iron, FIG. 1 is a perspective view, and FIG. 2 is a side view with a part broken away.
A plate-shaped ADI test piece (length 100 mm, width 100 mm, thickness 6 mm) was prepared and ultrasonically cleaned in acetone. The two washed ADI test pieces 1 and 1 were placed on the welding table 10 and the side surfaces 1a and 1a were butted against each other. At that time, an insert material 3 made of nickel (but containing inevitable impurities) was inserted between the both side surfaces (butting surfaces) 1a and 1a.

そして、両試験片１，１の側面１ａ，１ａの近傍部分及びインサート材３にレーザを照射して溶接を行った。レーザ溶接の条件は、溶接速度５００ｍｍ／ｍｉｎ、焦点位置−２ｍｍである。また、このレーザ溶接はシールドガス法により行い、シールドガスとしてヘリウムとアルゴンを用いた。図１，２に示すように、ヘリウムは流量３０Ｌ／ｍｉｎでレーザを照射している部分及びその周辺部に試験片１の上方から吹き付け、アルゴンは流量１０Ｌ／ｍｉｎで試験片１の下側に流した。   And the laser beam was irradiated to the vicinity part of the side surfaces 1a and 1a of both the test pieces 1 and 1, and the insert material 3, and it welded. The laser welding conditions are a welding speed of 500 mm / min and a focal position of −2 mm. The laser welding was performed by a shield gas method, and helium and argon were used as the shield gas. As shown in FIGS. 1 and 2, helium is sprayed from above the test piece 1 to the portion irradiated with the laser at a flow rate of 30 L / min and its peripheral portion, and argon is applied to the lower side of the test piece 1 at a flow rate of 10 L / min. Washed away.

レーザを照射すると、試験片１，１の側面１ａ，１ａの近傍部分とインサート材３とが共に溶融される。そして、レーザの照射を停止すると、溶融している部分が凝固して両試験片１，１が溶接される。
ＡＤＩは炭素や黒鉛を多量に含有しているため、インサート材３を用いずに溶接すると、溶融、凝固した部分（以降は溶融凝固部と記す）が白銑化して硬化し、溶接割れや気孔が発生した。そのため、一応接合はしたものの、接合部の強度は極めて低く、実用に耐え得るものではなかった。溶接割れの発生は、急熱，急冷による熱サイクルを受けて、溶融凝固部が著しく硬化したことが一因であると考えられる。 When the laser is irradiated, both the vicinity of the side surfaces 1a and 1a of the test pieces 1 and 1 and the insert material 3 are melted. When the laser irradiation is stopped, the melted portion is solidified and the two test pieces 1 and 1 are welded.
Since ADI contains a large amount of carbon and graphite, when it is welded without using the insert material 3, the melted and solidified portion (hereinafter referred to as the melt-solidified portion) turns white and hardens, resulting in weld cracks and pores. There has occurred. For this reason, although bonded once, the strength of the bonded portion was extremely low and could not withstand practical use. The occurrence of weld cracking is thought to be due to the fact that the melted and solidified portion has been significantly hardened due to thermal cycles due to rapid heating and rapid cooling.

一方、インサート材３を用いて溶接した場合は、ＡＤＩとニッケルとが共に溶融して混合されるため、溶融凝固部の組織はオーステナイト相を主とする組織となる。そのため、溶融凝固部の硬さが低くなって、溶接割れが抑制されたと考えられ、接合部の強度は、インサート材３を用いずに溶接した場合と比べて格段に高かった。
ＡＤＩ製試験片１に用いたＡＤＩ及びインサート材３に用いたニッケルの化学組成を表１に示す。また、溶融凝固部の化学組成を表２に示す。なお、シェフラー組織図による溶融凝固部のニッケル当量は３７．４であり、クロム当量は０．０２であった。 On the other hand, when welding is performed using the insert material 3, since the ADI and nickel are melted and mixed together, the structure of the melt-solidified portion is a structure mainly composed of the austenite phase. Therefore, it was considered that the hardness of the melt-solidified part was lowered and weld cracking was suppressed, and the strength of the joint part was much higher than when welding without using the insert material 3.
Table 1 shows the chemical composition of ADI used for the ADI test piece 1 and nickel used for the insert material 3. Table 2 shows the chemical composition of the melt-solidified part. In addition, the nickel equivalent of the melt-solidified part by a Schaeffler structure chart was 37.4, and the chromium equivalent was 0.02.

Figure 0005099543
Figure 0005099543

Figure 0005099543
Figure 0005099543

図３に、溶融凝固部の周辺部分の硬さ分布を示す。硬さの測定位置は、表面から１ｍｍ内部とした。インサート材３を用いずに溶接した場合の結果は、白丸印でプロットしてあるが、溶融凝固部（図３にはＦ．Ｚ．と記してある）の平均硬さは８２４Ｈｖで、熱影響部（図３にはＨ．Ａ．Ｚ．と記してある）の最高硬さは１１９２Ｈｖであり、５００Ｈｖ以下である元のＡＤＩの硬さよりも著しく硬化していることが分かる。これに対して、インサート材３を用いて溶接した場合は、黒丸印でプロットしてあるが、溶融凝固部の平均硬さは３９５Ｈｖで、熱影響部の最高硬さは１０４７Ｈｖであり、溶融凝固部の硬さは元のＡＤＩの硬さとほぼ同程度であることが分かる。   FIG. 3 shows the hardness distribution of the peripheral part of the melt-solidified part. The measurement position of hardness was 1 mm inside from the surface. The results of welding without using the insert material 3 are plotted with white circles, but the average hardness of the melt-solidified portion (indicated as F.Z. in FIG. 3) is 824 Hv, which is affected by heat. It can be seen that the maximum hardness of the part (indicated as HAZ in FIG. 3) is 1192 Hv, which is significantly harder than the original ADI hardness of 500 Hv or less. On the other hand, when welding using the insert material 3, it is plotted with black circles, but the average hardness of the melt-solidified portion is 395 Hv, and the maximum hardness of the heat-affected zone is 1047 Hv. It can be seen that the hardness of the part is approximately the same as that of the original ADI.

なお、インサート材３の素材はニッケルに限定されるものではなく、インサート材３を形成する金属がＡＤＩに混合されることにより溶融凝固部の組織が、オーステナイト相を主とする組織となるならば、他種の金属でも差し支えない。例えば、ニッケルを合金成分として含有する合金でもよいし、ニッケル及びクロムを合金成分として含有する合金でもよい。この合金においては、ニッケルが主成分であってもよいし、ニッケル以外の金属が主成分であってもよい。ニッケル以外の金属が主成分である合金としては、例えば鋼があげられる。このような鋼の具体例としては、ＳＵＳ３０４やＳＵＳ３１０Ｓがあげられる。
また、本実施形態においては、インサート材３の厚さを１．０ｍｍとしたが、溶融凝固部の組織がオーステナイト相を主とする組織となるならば、この厚さに限定されるものではない。 In addition, the raw material of the insert material 3 is not limited to nickel, and if the metal forming the insert material 3 is mixed with ADI, the structure of the melt-solidified portion becomes a structure mainly composed of an austenite phase. Other types of metals can be used. For example, an alloy containing nickel as an alloy component or an alloy containing nickel and chromium as an alloy component may be used. In this alloy, nickel may be the main component, or a metal other than nickel may be the main component. As an alloy whose main component is a metal other than nickel, for example, steel is cited. Specific examples of such steel include SUS304 and SUS310S.
In the present embodiment, the thickness of the insert material 3 is 1.0 mm. However, the thickness is not limited to this thickness as long as the structure of the melt-solidified portion is mainly austenite phase. .

さらに、本実施形態においては、ＡＤＩ製の部材同士を溶接する方法について説明したが、２つの部材のうち一方の部材がＡＤＩ製であれば、他方の部材は他種の金属（例えば球状黒鉛鋳鉄）製であっても、本発明の溶接方法を適用することができる。すなわち、オーステンパ球状黒鉛鋳鉄からなる部材と、他種の金属材料からなる部材とを突合せ、突合せ面の間にインサート材を挿入して前述のようにレーザ溶接を行えば、溶接割れ等の溶接欠陥をほとんど生じることなく両部材を溶接することができる。
以上説明したように、本発明のオーステンパ球状黒鉛鋳鉄の溶接方法によれば、溶接割れ等の溶接欠陥をほとんど生じることなくオーステンパ球状黒鉛鋳鉄を溶接することができる。よって、低強度の鋳鉄に代えて、オーステンパ球状黒鉛鋳鉄を自動車部品や構造部材の材料として適用することが可能となる。 Furthermore, in this embodiment, although the method of welding the members made from ADI was demonstrated, if one member is a product made from ADI among two members, the other member will be other types of metals (for example, spheroidal graphite cast iron) ), The welding method of the present invention can be applied. That is, if a member made of austempered spheroidal graphite cast iron and a member made of another type of metal material are butted together and an insert material is inserted between the butted surfaces and laser welding is performed as described above, welding defects such as weld cracks Both members can be welded with almost no occurrence.
As described above, according to the welding method for austempered spheroidal graphite cast iron of the present invention, austempered spheroidal graphite cast iron can be welded with almost no weld defects such as weld cracks. Therefore, it becomes possible to apply austempered spheroidal graphite cast iron as a material for automobile parts and structural members in place of low-strength cast iron.

本発明に係るオーステンパ球状黒鉛鋳鉄の溶接方法の一実施形態を説明する斜視図である。It is a perspective view explaining one embodiment of the welding method of austempered spheroidal graphite cast iron concerning the present invention. 本発明に係るオーステンパ球状黒鉛鋳鉄の溶接方法の一実施形態を説明する側面図である。It is a side view explaining one embodiment of the welding method of austempered spheroidal graphite cast iron concerning the present invention. 溶融凝固部の周辺部分の硬さ分布を示すグラフである。It is a graph which shows the hardness distribution of the peripheral part of a melt-solidification part.

符号の説明Explanation of symbols

１ ＡＤＩ製試験片
１ａ 側面（突合せ面）
３ インサート材 1 ADI specimen 1a Side (butting surface)
3 Insert material

Claims (2)

少なくとも一方がオーステンパ球状黒鉛鋳鉄からなる２つの部材を突合せ、そこにレーザを照射して前記両部材を溶接するに際して、前記両部材の突合せ面の間にインサート材を挿入してレーザを照射し、前記両部材の突合せ面近傍部分と前記インサート材とを共に溶融、凝固させ前記両部材を溶接するとともに、前記インサート材は、前記両部材の突合せ面近傍部分と前記インサート材とが溶融、凝固した溶融凝固部の組織が、オーステナイト相を主とする組織となるような金属からなり、該金属が、ニッケル及びクロムを合金成分として含有する鋼であることを特徴とするオーステンパ球状黒鉛鋳鉄の溶接方法。 At least one of the two members made of austempered spheroidal graphite cast iron is butted, and when the two members are welded by irradiating them with a laser, an insert material is inserted between the butt surfaces of the two members, and the laser is irradiated. The part near the butting surface of both members and the insert material are both melted and solidified to weld the both members, and the insert material is melted and solidified near the butting surface of the both members and the insert material. melt-solidified portion of the tissue, Ri Do a metal such as a tissue composed mainly of austenite phase, the metal is nickel and chromium austempered ductile iron characterized by Rukoto Oh in steel containing as alloying element Welding method. 前記鋼がＳＵＳ３１０Ｓであることを特徴とする請求項１に記載のオーステンパ球状黒鉛鋳鉄の溶接方法。 Welding method of austempered ductile iron according to claim 1, wherein the steel is characterized SUS310S der Rukoto.
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