JP3848871B2 - Brazing method using iron brazing material and iron brazing material - Google Patents
Brazing method using iron brazing material and iron brazing material Download PDFInfo
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- JP3848871B2 JP3848871B2 JP2001366978A JP2001366978A JP3848871B2 JP 3848871 B2 JP3848871 B2 JP 3848871B2 JP 2001366978 A JP2001366978 A JP 2001366978A JP 2001366978 A JP2001366978 A JP 2001366978A JP 3848871 B2 JP3848871 B2 JP 3848871B2
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- 239000000463 material Substances 0.000 title claims description 114
- 238000005219 brazing Methods 0.000 title claims description 112
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims description 61
- 229910052742 iron Inorganic materials 0.000 title claims description 31
- 238000000034 method Methods 0.000 title claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 23
- 229910052799 carbon Inorganic materials 0.000 claims description 14
- 238000005496 tempering Methods 0.000 claims description 10
- 238000010791 quenching Methods 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 8
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 description 28
- 239000010959 steel Substances 0.000 description 28
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 239000002184 metal Substances 0.000 description 12
- 229910052751 metal Inorganic materials 0.000 description 12
- 239000000945 filler Substances 0.000 description 11
- 229910052804 chromium Inorganic materials 0.000 description 10
- 230000000694 effects Effects 0.000 description 8
- 229910000734 martensite Inorganic materials 0.000 description 8
- 238000002844 melting Methods 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 229910052750 molybdenum Inorganic materials 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 229910000851 Alloy steel Inorganic materials 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 150000002505 iron Chemical class 0.000 description 3
- 229910000975 Carbon steel Inorganic materials 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 2
- 239000010962 carbon steel Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000010606 normalization Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000005476 soldering Methods 0.000 description 1
- 238000000108 ultra-filtration Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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- Pressure Welding/Diffusion-Bonding (AREA)
- Heat Treatment Of Articles (AREA)
Description
【０００１】
【発明の属する技術分野】
本発明は、鉄系低合金を素材にした鉄系ろう材に関し、さらに具体的にはろうずけ接合した後ろうずけ接合した母材を熱処理することによって、高強度及び高靭性を備えることができる鉄系ろう材、及びこの鉄系ろう材を用いたろう付け方法に関する。
【０００２】
【従来の技術】
従来、鉄鋼材料のろう付けにはＮｉ系ろう材が用いられてきたが、しかしながらこのＮｉ系ろう材は接合された鉄鋼材料のろう材部を高強度にすることはことはできるが、そのろう材部に高靭性を備えることができなかった。
【０００３】
また、鉄鋼材料のろう付けに金系ろう材を用いた場合、ろう材部は鉄鋼材料により変形が拘束されるので、ろう材部自体の強度を確保することがきるが、Ｎｉ系ろう材と同様にろう材部に高靭性を備えることはできなかった。
【０００４】
また、特開平６−１５４７９号公報には、Ｎｉ−Ｃｒ−Ｍｏ含有合金鋼をろう材素材とし、且つ、０．５ｗｔ％≦Ｃ≦２．０ｗｔ％、３．０ｗｔ％≦Ｂ≦３．５ｗｔ％、及び４．０ｗｔ％≦Ｓｉ≦４．３ｗｔ％を添加することによって、１０５０℃〜１０６０℃程度の低融点でろう付けが可能である鉄系ろう付け材が開示されている。しかしながら、上記ろう材を構造用鋼と使用する鉄鋼材料のろう付け接合に用いた場合、課題となるろう材部の衝撃値向上に関してはなんら言及をしていない。
【０００５】
【発明が解決しようとする課題】
上記状況を鑑み、本発明者は、鉄鋼材料をより低温度でろう付けすることにより、並びにろう付け後に種々の熱処理をろう付けした材料に施すことによって高強度及び鋼靭性を材料に付与することができることに着目した。本発明の鉄系ろう材は、構造用鋼として使用する鉄鋼材料を１２００℃以下の低い温度でろう付けすることを可能にし、且つ接合されたろう材部に種々の熱処理を行ない高強度及び高靭性を付与することが可能とすることを目的とする。
【０００６】
【課題を解決するための手段】
上記課題は、本発明の下記の鉄系ろう材及びこの鉄系ろう付け材を用いたろう付け方法によって達成することができる。
【０００７】
本発明の鉄系ろう材は、０．５〜１．５ｗｔ％のＢ、１．５〜３．０ｗｔ％のＳｉ及び１．０〜３．５ｗｔ％のＣを含有し残部がＦｅからなるものである。また、これに加えて、１．５〜３．５ｗｔ％のＮｉ及び０．５〜１．０ｗｔ％のＣｒを含有する材料である場合、ろう付け後にさらに熱処理を施すことによって衝撃値を改善する効果が著しい。
【０００８】
さらに、０．５〜１．５ｗｔ％のＢ、１．５〜３．０ｗｔ％のＳｉ、１．０〜３．５ｗｔ％のＣ、１．５〜３．５ｗｔのＮｉ、０．５〜１．０ｗｔ％のＣｒ及び０．１〜０．３ｗｔ％のＭｏを含有し残部がＦｅからなる材料である場合、ろう付け後にさらに熱処理を施すことによってさらに衝撃値を改善する効果が得られる。
【０００９】
また、本発明のろう付け方法は、上記ろう材を用いて接合される母材同士をろう付けした後、接合された母材を熱処理する。さらに、本発明のろう付け方法は、上記熱処理が、焼入れ焼き戻し熱処理であることを特徴とする。さらに、本発明のろう付け方法は、上記熱処理が、焼ならし焼き戻し熱処理であることを特徴とする。
【００１０】
【発明の実施の形態】
本発明の鉄系ろう材は、鉄系低合金をろう材の基本材とし、これらの合金に０．５〜１．５ｗｔ％のＢ、１．５〜３．０ｗｔ％のＳｉ及び１．０〜３．５ｗｔの％Ｃを添加したろう材であって、この鉄系ろう材の融点は１０００℃から１２００℃の範囲に存在する。また、本発明の鉄系ろう材は、上記Ｂ、Ｓｉ及びＣを含有する材料を溶融急冷法により製作する。なお、本発明の好ましいろう材の基本となる合金はＮｉ−Ｃｒ系であって１．５〜３．５ｗｔ％のＮｉ及び０．５〜１．０ｗｔ％のＣｒを含有する合金であり、さらに０．５〜１．５ｗｔ％のＢ、１．５〜３．０ｗｔ％のＳｉ及び１．０〜３．５ｗｔ％のＣを添加した合金である。
【００１１】
本発明のろう付け接合においては、Ｎｉ−Ｃｒ−Ｍｏ鋼（ＳＮＣＭ鋼）、炭素鋼及び低合金鋼をろう付け接合する母材とし、このろう付け接合される鋼材試料は、接合面となる面を所定の平面加工を行なう。用意したろう付け接合鋼材試料は、互いの加工平面の間に例えば総厚さ１００ミクロンの鉄系ろう材をはさみ、自重程度の圧力を加えて、６．７×１０-2Ｐａ（５×１０-4Ｔｏｒｒ）以下の真空中でろう付け作業を行なう。それによって、ろう材とろう付け接合鋼材試料との接合面は、良好な濡れ性を示してろう付け接合することができる。互いのろう付け接合鋼材試料との間に形成されるろう材部は、この鋼材試料より高含有量のろう材中の成分すなわちＢ、Ｓｉ及びＣが、鋼材試料中に拡散浸透して、ろう材とろう付け接合される鋼材試料とはほぼ同等の化学組成となる。しかし、ろう材中のＳｉはろう付け接合される鋼材試料への拡散速度が遅いために、ろう材のＳｉ添加量はろう付け接合される鋼材試料より過度に多くならないように調整する必要がある。ろう付け接合される鋼材試料の間にろう材によって形成されるろう材部の組成は、ろう付け後の焼入れ時の加熱によってろう材中の高濃度成分がさらにろう付け接合される鋼材試料中へと拡散浸透して、ろう材部はろう付け接合される鋼材試料と同等の化学組成となる。通常の炭素鋼の場合は、ろう材中への拡散速度が遅く且つ多量に含有されると衝撃値に悪影響を及ぼすＳｉを１．５〜３ｗｔ％と低くしているので、従来のろう材の比べて衝撃値が改善される。熱処理を行うと衝撃値がさらに改善される。
【００１２】
そして、ろう材中に１．５〜３．５ｗｔ％のＮｉ、０．５〜１．５ｗｔ％のＣｒ及び０．５〜１．５ｗｔ％のＢ、１．５〜３．０ｗｔ％のＳｉ、１．０〜３．５ｗｔ％のＣを含有し、被接合材がＳＮＣＭ４３１のような材料の場合は、ろう付け接合されたろう付け部は、その後の焼入れ焼き戻し熱処理により、ろう付け接合される鋼材試料と同等の焼き戻しマルテンサイト組織となる。ろう付け接合される鋼材試料と同等の焼き戻しマルテンサイト組織となったろう材部は、９０ｋｇｆ／ｍｍ2以上の引張強さの強度が達成されるとともに、２ｖＥ０値（２ｍｍＶノッチシャルピー衝撃値）が２１Ｊ以上の衝撃値を達成することができる。さらに、本発明においてろう材の成分範囲を特定の範囲とした場合、２ｖＥ０値が２７Ｊ以上の衝撃値を達成することができる。
【００１３】
また、焼きならし及び焼き戻し熱処理により焼き戻しマルテンサイト組織となったろう材部は、８０ｋｇｆ／ｍｍ2以上の引張強さの強度が達成されるとともに、２ｖＥ０値が２１Ｊ以上の衝撃値を達成することができる。本実施例では２９Ｊを達成した。
【００１４】
【実施例】
実施例１
本発明の表１に示す各成分組成のろう材を用いて、ＳＮＣＭ４３１鋼のろう付け接合母材をろう付けをした。１１８０℃または１２００℃の温度でろう付けしてその後８５７℃で焼入れを施しその後さらに６００℃で焼き戻した熱処理を施した試料を表１にＱ＆Ｔで示す。また、１１８０℃または１２００℃の温度でろう付け後さらに８５７℃で焼きならし及び６００℃で焼き戻し熱処理を施した試料を表３にＮ及びＴで示す。これらの条件でろう付け後各熱処理を施した各試料の、シャルピー衝撃値を表２及び表４に示す。
【００１５】
表１ろう付け試験結果
No 区分 ろう材 接合 熱 備考
温度 処理
1 本 Fe-1.7Ni-0.7Cr-2Si-1B-3C 1180℃ Q&T 代表値
2 発 Fe-2Ni-0.5Cr-3Si-0.5B-1C 1200℃ Q&T Si上限B,C下限
3 明 Fe-2Ni-0.5Cr-3Si-0.5B-3.5C 1180℃ Q&T C,Si上限B下限
4 〃 Fe-2Ni-0.5Cr-3Si-1.5B-1C 1200℃ Q&T Si,B上限C下限
5 〃 Fe-2Ni-0.5Cr-3Si-1.5B-1C 1200℃ Q&T Si,B,C上限
6 〃 Fe-2Ni-0.5Cr-1.5Si-1.5B-1C 1200℃ Q&T B上限Si,C下限
7 〃 Fe-2Ni-0.5Cr-1.5Si-0.5B-3.5C 1200℃ Q&T C 上限Si,B下限
8 〃 Fe-2Ni-0.5Cr-1.5Si-1.5B-3.5C 1200℃ Q&T B,C上限Si下限
9 〃 Fe-2Ni-0.5Cr-1.5Si-0.5B-1C 1200℃ Q&T Si,B,C上限
10 〃 Fe-3.5Ni-0.5Cr-0.2Mo-1.5Si-0.5B-1C 1200℃ Q&T Ni高 Cr低
11 〃 Fe-3.5Ni-1.5Cr-0.1Mo-1.5Si-1.5B-3.5C1200℃ Q&T Ni,Cr 高Mo低
12 〃 Fe-3.5Ni-1Cr-0.3Mo-1.5Si-0.5B-1C 1200℃ Q&T Ni,Cr,Mo高
13 〃 Fe-2Ni-1Cr-0.1Mo-1.5Si-1.5B-3.5C 1200℃ Q&T Cr高Mo低
14 〃 Fe-2Ni-0.5Cr-0.3Mo-3Si-1.5B-3.5C 1200℃ Q&T Mo高Cr低
15 〃 Fe-1.6Ni-0.5Cr-0.1Mo-3Si-1.5B-3.5C 1200℃ Q&T Ni,Cr,Mo低
16 〃 Fe-1.6Ni-1Cr-0.1Mo-3Si-1.5B-3.5C 1200℃ Q&T Cr高Ni,Mo低
17 〃 Fe-1.6Ni-0.5Cr-0.3Mo-3Si-1.5B-3.5C 1200℃ Q&T Mo高Ni,Cr低
18 〃 Fe-2.0Ni-1.5Cr-3Si-0.5B-2.3C 1200℃ Q&T Cr特定範囲
上限外
19 〃 Fe-2.0Ni-1.5Cr-0.5Mo-3Si-0.5B-2.3C 1200℃ Q&T Cr特定範囲
下限外
20 〃 Fe-2.0Ni-0.2Cr-0.5Mo-3Si-0.5B-2.3C 1200℃ Q&T Cr特定範囲
上限外
21 〃 Fe-1.2Ni-0.5Cr-3Si-0.5B-3.0C 1200℃ Q&T Ni特定範囲
下限外
22 〃 Fe-4.0Ni-1.0Cr-3Si-0.5B-2.3C 1200℃ Q&T Ni特定範囲
上限外
23 〃 Fe-4Ni-1.5Cr-1Si-1.5B-3C 1200℃ Q&T Ni,Cr 特定範囲
上限外
24 〃 Fe-1Mn-1.2Cr-1Si-1.5B-3C 1200 ℃ Q&T Ni,Mo 含まず
25 本 Fe-2Ni-0.5Cr-2Si-1B-3C 1200℃ ろう付熱処理範囲外
26 発 Fe-1.7Ni-1Cr-0.2Mo-5Si-2.3C 1200℃ Q&T Si範囲上限外
27 明 Fe-2Ni-0.7Cr-2.0Si-0.3B-2C 1200℃ Q&T B範囲下限外
28 外 Fe-2Ni-0.5Cr-2Si-1B-4C 1200℃ Q&T C範囲上限外
29 〃 Fe-1.2Ni-0.7Cr-0.3Mo-2.0Si-3B-2.3C 1200℃ Q&T B範囲上限外
30 〃 Fe-2Ni-0.5Cr-2Si-1B-0.5C 1200℃ Q&T C範囲下限外
31 〃 Fe-2Ni-0.7Cr-1.0Si-1B-2C 1200 ℃ Q&T Si 範囲下限外
本発明の鉄系ろう材を用いてろう付け接合された母材は、焼入れ焼き戻し熱処理、または焼きならし焼き戻し熱処理を施すことによって、表２及び表４に示すように有用な強度レベルのシャルピー衝撃値を得ることができた。本発明の鉄系ろう材は、鉄系低合金鋼にＢを０．５〜１．５ｗｔ％、Ｓｉを１、５〜３．０ｗｔ％、Ｃを１．０〜３．５ｗｔ％を添加することを特徴とする。
【００１６】
【００１７】
Ｓｉはろう材の融点を低下させるので、Ｓｉの含有量は１．５ｗｔ％以上とする。しかしながら、Ｓｉはろう材及びろう付け接合母材中への拡散速度が遅く、且つ３ｗｔ％以上を含有すると、図２の組織模式図に示すように、ろう材部が焼き戻しマルテンサイトに変態することなくフェライト相が生じることになり、シャルピー衝撃値が向上しなくなる。したがって、本発明のろう材は、Ｓｉの含有量を１．５ｗｔ％〜３ｗｔ％の範囲とするのが好ましい。ＣもＢと同様にろう材の融点の低下をもたらし且つろう付け接合母材へと拡散することによってろう付け部のシャルピー衝撃値を改善するので、ろう材に１．０ｗｔ％以上のＣを含有させる。しかしながら、Ｃの含有量が３．５ｗｔ％を越えるとシャルピー衝撃値が向上しなくなる。したがって、本発明のろう材は、Ｃの含有量を１．０〜３．５ｗｔ％の範囲とする。以上のように鉄系低合金に０．５〜１．５ｗｔ％のＢ、１．５〜３ｗｔ％のＳｉ、１．０〜３．５ｗｔ％のＣを含むろう材であることを基本とする。
【００１８】
図１には、本発明の効果を高める材料としてＳＮＣＭ４３１銅に２ｗｔ％Ｓｉ−１ｗｔ％Ｂ−３ｗｔ％Ｃを含有するろう材で、ろう付け接合する母材がＮｉ−Ｃｒ−Ｍｏ鋼（ＳＮＣＭ鋼）である継手を接合した断面組織の模式図である。この断面組織の模式図においては、ろう付け接合母材とろう材部とがともに細かい焼き戻しマルテンサイト組織となっていることが示されている。
【００１９】
この材料のろう付け部は、ろう付け部に焼き戻しマルテンサイトを得ることにより衝撃値を著しく改善する効果を有する。
【００２０】
また、接合される継手に高強度及び高靭性が必要な場合は、本発明のろう材の素材である鉄系低合金に含有されるＮｉを１．５〜３．５ｗｔ％、Ｃｒを０．５〜１．０ｗｔ％とし、この鉄系低合金にＢを０．５〜１．５ｗｔ％、Ｓｉを１、５〜３．０ｗｔ％、Ｃを１．０〜３．５ｗｔ％を添加すればよい（表１：Ｎｏ．１〜Ｎｏ．１７参照）。
【００２１】
さらに好ましくは、本発明のろう材の素材である鉄系低合金に含有されるＮｉを１．５〜３．５ｗｔ％、Ｃｒを０．５〜１．０ｗｔ％、Ｍｏを０．１〜０．３ｗｔ％とし、この鉄系低合金にＢを０．５〜１．５ｗｔ％、Ｓｉを１、５〜３．０ｗｔ％、Ｃを１．０〜３．５ｗｔ％を添加する（表１：Ｎｏ．１〜Ｎｏ．１７参照）。
【００２２】
上記のように本発明のろう材の素材である鉄系低合金のＮｉ、Ｃｒ、さらにＭｏの添加量を限定することによって、焼入れ性の増加とともに焼き戻し脆化の低減とを達成できる。
【００２３】
Ｎｉの添加量が１．５ｗｔ％より少ないと焼入れ時或いは焼きならし時に冷却速度が遅くなった場合に、ろう材部は十分な量のマルテンサイト組織に変態せず、高強度が得られなくなる。また、Ｎｉの添加量が３．５ｗｔ％を越えると焼き戻し脆化が著しくなり、高いシャルピー衝撃値が得られなくなる。したがって、本発明のろう材の素材である鉄系低合金のＮｉ添加量は、１．５〜３．５ｗｔ％の範囲とするとより好ましい。
【００２４】
Ｃｒを０．５ｗｔ％以上添加すると焼入れ性の向上に効果があるが、１．０ｗｔ％を越えるとシャルピー衝撃値の向上に効果が期待できなくなる。したがって、本発明のろう材の素材である鉄系低合金のＣｒ添加量は、０．５〜１．０ｗｔ％の範囲とするとより好ましい。
【００２５】
ＭｏもＣｒと同様に焼き入れ性の改善に効果があるが、Ｍｏ含有量が０．１ｗｔ％以下では焼入れ性の改善に効果を示さない。Ｍｏは高価であるうえに、Ｍｏ含有量が０．３ｗｔ％を越えると熱処理温度が変化した場合に焼き戻し硬化を生じて、熱処理温度と引張強さ、シャルピー衝撃値とが対応しにくくなる。したがって、本発明のろう材の素材である鉄系低合金のＭｏ添加量は、０．１〜０．３ｗｔ％の範囲とするとより好ましい。
【００２６】
【発明の効果】
上記のように、本発明のろう材は、Ｂ、Ｓｉ及びＣを含有し、残部をＦｅとすることによって、融点を低下させてろう付けを可能にすることができる。さらに、Ｎｉ、ＣｒまたはＭｏを適正範囲で含有することによって、焼入れ性を向上させ、焼き戻し脆化を緩和することができる。すなわち、標準状態では構造用合金と同様のフェライト−パーライト系組織でありながら、構造用合金と同様に焼入れ後或いは焼きならし処理後の焼き戻し処理により、焼き戻しマルテンサイト組織を得ることができ、シャルピー衝撃値を向上することが可能となった。
【図面の簡単な説明】
【図１】図１は、本発明のろう付け材を用いて接合した母材とろう材部との断面組織を示す模式図である。
【図２】図２は、従来技術のろう付け材を用いて接合した母材とろう材部との断面組織を示す模式図である。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to an iron-based brazing material made of an iron-based low alloy, and more specifically, having high strength and high toughness by heat-treating the base material that has been solder-joined after soldering. The present invention relates to an iron-based brazing material that can be used, and a brazing method using the iron-based brazing material.
[0002]
[Prior art]
Conventionally, a Ni-based brazing material has been used for brazing a steel material. However, this Ni-based brazing material can increase the strength of the brazing material portion of the joined steel material. The material part could not have high toughness.
[0003]
In addition, when a metal brazing material is used for brazing a steel material, deformation of the brazing material portion is restrained by the steel material, so that the strength of the brazing material portion itself can be secured. Similarly, the brazing filler metal part could not be provided with high toughness.
[0004]
Japanese Patent Laid-Open No. 6-15479 discloses a Ni—Cr—Mo containing alloy steel as a brazing material, and 0.5 wt% ≦ C ≦ 2.0 wt%, 3.0 wt% ≦ B ≦ 3.5 wt. %, And 4.0 wt% ≦ Si ≦ 4.3 wt%, an iron-based brazing material that can be brazed at a low melting point of about 1050 ° C. to 1060 ° C. is disclosed. However, when the brazing material is used for brazing and joining of the steel material to be used with the structural steel, no mention is made regarding the improvement of the impact value of the brazing material portion, which is a problem.
[0005]
[Problems to be solved by the invention]
In view of the above situation, the present inventor imparts high strength and steel toughness to the material by brazing the steel material at a lower temperature and by applying various heat treatments to the brazed material after brazing. Focused on being able to. The iron-based brazing material of the present invention makes it possible to braze a steel material used as a structural steel at a low temperature of 1200 ° C. or less, and performs various heat treatments on the joined brazing material portion to provide high strength and high toughness. The purpose is to make it possible to grant.
[0006]
[Means for Solving the Problems]
The above object can be achieved by the following iron-based brazing material of the present invention and a brazing method using this iron-based brazing material.
[0007]
Iron-based brazing material of the present invention, 0. 5～1.5Wt% B, with a remainder containing C of 1.5～3.0Wt% of Si and 1.0～3.5Wt% is Fe Tona shall. In addition to this, when a material containing 1.5～3.5Wt% of Ni and 0.5 to 1.0% of Cr, to improve the impact value by performing further heat treatment after brazing The effect is remarkable.
[0008]
Furthermore, 0.5 to 1.5 wt% B, 1.5 to 3.0 wt% Si, 1.0 to 3.5 wt% C, 1.5 to 3.5 wt Ni, 0.5 to 1 If the balance contained .0Wt% of Cr and 0.1 to 0.3% of Mo is Ru Fe Tona material, the effect of further improving the impact value by performing further heat treatment after brazing is obtained.
[0009]
Moreover, the brazing method of this invention heat-processes the joined base material, after brazing the base materials joined using the said brazing material. Furthermore, the brazing method of the present invention is characterized in that the heat treatment is a quenching and tempering heat treatment. Furthermore, the brazing method of the present invention is characterized in that the heat treatment is a normalizing and tempering heat treatment.
[0010]
DETAILED DESCRIPTION OF THE INVENTION
The iron-based brazing material of the present invention uses an iron-based low alloy as a basic material of the brazing material, and 0.5 to 1.5 wt% B, 1.5 to 3.0 wt% Si and 1.0 are added to these alloys. A brazing material to which ˜3.5 wt% C is added, and the melting point of this iron-based brazing material is in the range of 1000 ° C. to 1200 ° C. The iron-based brazing material of the present invention is produced by melting and quenching the material containing B, Si and C. The alloy that is the basis of the preferred brazing filler metal of the present invention is an Ni-Cr-based alloy containing 1.5 to 3.5 wt% Ni and 0.5 to 1.0 wt% Cr, It is an alloy to which 0.5 to 1.5 wt% B, 1.5 to 3.0 wt% Si and 1.0 to 3.5 wt% C are added.
[0011]
In the brazing joint of the present invention, Ni—Cr—Mo steel (SNCM steel), carbon steel and low alloy steel are used as a base material for brazing, and the steel material to be brazed is a surface to be a joining surface. A predetermined plane processing is performed. The prepared brazed steel sample is sandwiched between, for example, an iron-based brazing material having a total thickness of 100 microns between the processing planes, and a pressure of about its own weight is applied, so that 6.7 × 10 −2 Pa (5 × 10 5 -4 Torr) Perform brazing in the following vacuum. As a result, the joint surface between the brazing material and the brazed joint steel material sample exhibits good wettability and can be brazed. In the brazing filler metal part formed between the brazed steel samples, the components in the brazing material having a higher content than that of the steel sample, that is, B, Si and C, diffuse and penetrate into the steel sample. The steel material to be brazed and joined to the steel has almost the same chemical composition. However, since Si in the brazing material has a low diffusion rate into the steel material to be brazed, it is necessary to adjust the amount of Si added to the brazing material so that it does not become excessively larger than the steel material to be brazed. . The composition of the brazing filler metal part formed by the brazing material between the steel samples to be brazed and joined is a steel sample in which high concentration components in the brazing material are further brazed and joined by heating during quenching after brazing. The brazing material portion has a chemical composition equivalent to that of the steel material to be brazed. In the case of ordinary carbon steel, since the diffusion rate into the brazing material is slow and a large amount is contained, Si which has an adverse effect on the impact value is lowered to 1.5 to 3 wt%. Compared to the impact value. The impact value is further improved by heat treatment.
[0012]
And 1.5 to 3.5 wt% Ni, 0.5 to 1.5 wt% Cr and 0.5 to 1.5 wt% B, 1.5 to 3.0 wt% Si in the brazing material, In the case of containing 1.0 to 3.5 wt% of C and the material to be joined is a material such as SNCM431, the brazed portion that is brazed and joined is a steel material that is brazed and joined by a subsequent quenching and tempering heat treatment. A tempered martensite structure equivalent to the sample is obtained. The brazing material portion having a tempered martensite structure equivalent to the steel material to be brazed and joined has achieved a tensile strength of 90 kgf / mm 2 or more and a 2vE0 value (2 mmV notch Charpy impact value) of 21 J. The above impact value can be achieved. Furthermore, when the component range of the brazing filler metal is set to a specific range in the present invention, an impact value with a 2vE0 value of 27 J or more can be achieved.
[0013]
Further, the brazing filler metal part having a tempered martensite structure by normalizing and tempering heat treatment achieves a tensile strength of 80 kgf / mm 2 or more and an impact value of 2VE0 of 21 J or more. be able to. In this example, 29 J was achieved.
[0014]
【Example】
Example 1
The brazing joint base material of SNCM431 steel was brazed using the brazing material having each component composition shown in Table 1 of the present invention. Table 1 shows the Q & T of the heat-treated samples that were brazed at a temperature of 1180 ° C. or 1200 ° C., then quenched at 857 ° C. and then tempered at 600 ° C. Samples subjected to brazing at a temperature of 1180 ° C. or 1200 ° C. and further subjected to normalization at 857 ° C. and tempering heat treatment at 600 ° C. are indicated by N and T in Table 3. Tables 2 and 4 show the Charpy impact values of the samples subjected to each heat treatment after brazing under these conditions.
[0015]
Table 1 Brazing test results
No Category Brazing material Joining heat Remarks
Temperature treatment
1 piece Fe-1.7Ni-0.7Cr-2Si-1B-3C 1180 ° C Q & T typical value
2 shots Fe-2Ni-0.5Cr-3Si-0.5B-1C 1200 ° C Q & T Si upper limit B, C lower limit
3 Bright Fe-2Ni-0.5Cr-3Si-0.5B-3.5C 1180 ° C Q & T C, Si upper limit B lower limit
4 〃 Fe-2Ni-0.5Cr-3Si-1.5B-1C 1200 ° C Q & T Si, B upper limit C lower limit
5 〃 Fe-2Ni-0.5Cr-3Si-1.5B-1C 1200 ° C Q & T Si, B, C upper limit
6 〃 Fe-2Ni-0.5Cr-1.5Si-1.5B-1C 1200 ° C Q & T B upper limit Si, C lower limit
7 〃 Fe-2Ni-0.5Cr-1.5Si-0.5B-3.5C 1200 ° C Q & T C upper limit Si, B lower limit
8 〃 Fe-2Ni-0.5Cr-1.5Si-1.5B-3.5C 1200 ° C Q & T B, C upper limit Si lower limit
9 〃 Fe-2Ni-0.5Cr-1.5Si-0.5B-1C 1200 ° C Q & T Si, B, C upper limit
10 〃 Fe-3.5Ni-0.5Cr-0.2Mo-1.5Si-0.5B-1C 1200 ° C Q & T Ni High Cr Low
11 〃 Fe-3.5Ni -1.5 Cr-0.1Mo-1.5Si-1.5B-3.5C 1200 ° C Q & T Ni, Cr High Mo Low
12 〃 Fe-3.5Ni-1Cr-0.3Mo-1.5Si-0.5B-1C 1200 ° C Q & T Ni, Cr, Mo high
13 〃 Fe-2Ni-1Cr-0.1Mo-1.5Si-1.5B-3.5C 1200 ° C Q & T Cr High Mo Low
14 〃 Fe-2Ni-0.5Cr-0.3Mo-3Si-1.5B-3.5C 1200 ° C Q & T Mo High Cr Low
15 〃 Fe-1.6Ni-0.5Cr-0.1Mo-3Si-1.5B-3.5C 1200 ° C Q & T Ni, Cr, Mo low
16 〃 Fe-1.6Ni-1Cr-0.1Mo-3Si-1.5B-3.5C 1200 ° C Q & T Cr high Ni, Mo low
17 〃 Fe-1.6Ni-0.5Cr-0.3Mo-3Si-1.5B-3.5C 1200 ° C Q & T Mo high Ni, Cr low
18 〃 Fe-2.0Ni-1.5Cr-3Si-0.5B-2.3C 1200 ° C Q & T Cr specific range
Outside the upper limit
19 〃 Fe-2.0Ni-1.5Cr-0.5Mo-3Si-0.5B-2.3C 1200 ° C Q & T Cr specific range
Outside the lower limit
20 〃 Fe-2.0Ni-0.2Cr-0.5Mo-3Si-0.5B-2.3C 1200 ° C Q & T Cr specific range
Outside the upper limit
21 〃 Fe-1.2Ni-0.5Cr-3Si-0.5B-3.0C 1200 ° C Q & T Ni specific range
Outside the lower limit
22 〃 Fe-4.0Ni-1.0Cr-3Si-0.5B-2.3C 1200 ° C Q & T Ni specific range
Outside the upper limit
23 〃 Fe-4Ni-1.5Cr-1Si-1.5B-3C 1200 ° C Q & T Ni, Cr Specific range
Outside the upper limit
24 〃 Fe-1Mn-1.2Cr-1Si-1.5B-3C 1200 ℃ Q & T Ni, Mo not included
25 Fe-2Ni-0.5Cr-2Si-1B-3C 1200 ° C Out of brazing heat treatment range
26 Fe-1.7Ni-1Cr-0.2Mo-5Si-2.3C 1200 ° C Q & T Si out of upper limit
27 Akira Fe-2Ni-0.7Cr-2.0Si- 0.3B-2C 1200 ℃ Q & T B range under ultrafiltration
28 Outer Fe-2Ni-0.5Cr-2Si-1B-4C 1200 ° C Q & T C Out of upper limit
29 〃 Fe-1.2Ni-0.7Cr-0.3Mo-2.0Si-3B-2.3C 1200 ° C Q & T B out of upper limit
30 〃 Fe-2Ni-0.5Cr-2Si-1B-0.5C 1200 ° C Q & T C Out of range
31 〃 Fe-2Ni-0.7Cr-1.0Si-1B-2C 1200 ℃ Q & T Outside the Si range lower limit The base material brazed using the iron-based brazing material of the present invention is useful as shown in Tables 2 and 4 by performing quenching and tempering heat treatment or normalizing and tempering heat treatment. A Charpy impact value with a proper strength level could be obtained. In the iron-based brazing material of the present invention, 0.5 to 1.5 wt% of B, 1, 5 to 3.0 wt% of Si, and 1.0 to 3.5 wt% of C are added to the iron-based low alloy steel. It is characterized by that.
[0016]
[0017]
Since Si lowers the melting point of the brazing material, the Si content is 1.5 wt% or more. However, when Si has a slow diffusion rate into the brazing material and the brazing joint base material and contains 3 wt% or more, the brazing material portion is transformed into tempered martensite as shown in the schematic structure diagram of FIG. Without this, the ferrite phase is generated, and the Charpy impact value is not improved. Therefore, the brazing filler metal of the present invention preferably has a Si content in the range of 1.5 wt% to 3 wt%. C, like B, causes a decrease in the melting point of the brazing material and improves the Charpy impact value of the brazing portion by diffusing into the brazing joint base material. Therefore, the brazing material contains 1.0 wt% or more of C. Let However, when the C content exceeds 3.5 wt%, the Charpy impact value is not improved. Therefore, the brazing filler metal of the present invention has a C content in the range of 1.0 to 3.5 wt%. As described above, it is basically a brazing material containing 0.5 to 1.5 wt% B, 1.5 to 3 wt% Si, and 1.0 to 3.5 wt% C in an iron-based low alloy. .
[0018]
FIG. 1 shows a brazing material containing 2 wt% Si-1 wt% B-3 wt% C in SNCM431 copper as a material for enhancing the effect of the present invention, and the base material to be brazed is Ni-Cr-Mo steel (SNCM steel). It is a schematic diagram of the cross-sectional structure | tissue which joined the joint which is). In the schematic diagram of the cross-sectional structure, it is shown that both the brazing joint base material and the brazing material part have a fine tempered martensite structure.
[0019]
The brazed part of this material has the effect of significantly improving the impact value by obtaining tempered martensite in the brazed part.
[0020]
Further, when high strength and high toughness are required for the joint to be joined, 1.5 to 3.5 wt% of Ni contained in the iron-based low alloy that is the material of the brazing material of the present invention, and Cr of 0.1%. 5 to 1.0 wt%, B is added to 0.5 to 1.5 wt%, Si is added to 1 to 5 to 3.0 wt%, and C is added to 1.0 to 3.5 wt%. Good (see Table 1: No. 1 to No. 17).
[0021]
More preferably, Ni contained in the iron-based low alloy that is the material of the brazing material of the present invention is 1.5 to 3.5 wt%, Cr is 0.5 to 1.0 wt%, and Mo is 0.1 to 0. .3 wt%, and 0.5 to 1.5 wt% of B, 1, 5 to 3.0 wt% of Si, and 1.0 to 3.5 wt% of C are added to this iron-based low alloy (Table 1: No. 1 to No. 17).
[0022]
As described above, by limiting the amount of addition of Ni, Cr, and Mo of the iron-based low alloy that is the material of the brazing material of the present invention, it is possible to achieve an increase in hardenability and a reduction in temper embrittlement.
[0023]
If the amount of Ni added is less than 1.5 wt%, the brazing filler metal part will not be transformed into a sufficient amount of martensite structure and high strength will not be obtained when the cooling rate becomes slow during quenching or normalizing. . On the other hand, when the added amount of Ni exceeds 3.5 wt%, temper embrittlement becomes remarkable and a high Charpy impact value cannot be obtained. Therefore, the Ni addition amount of the iron-based low alloy that is the material of the brazing material of the present invention is more preferably in the range of 1.5 to 3.5 wt%.
[0024]
If Cr is added in an amount of 0.5 wt% or more, it is effective for improving the hardenability, but if it exceeds 1.0 wt%, an effect for improving the Charpy impact value cannot be expected. Therefore, the Cr addition amount of the iron-based low alloy that is the material of the brazing material of the present invention is more preferably in the range of 0.5 to 1.0 wt%.
[0025]
Mo is also effective in improving the hardenability like Cr, but if the Mo content is 0.1 wt% or less, there is no effect in improving the hardenability. In addition to being expensive, if the Mo content exceeds 0.3 wt%, temper hardening occurs when the heat treatment temperature changes, making it difficult to correspond to the heat treatment temperature, tensile strength, and Charpy impact value. Therefore, it is more preferable that the Mo addition amount of the iron-based low alloy that is the material of the brazing filler metal of the present invention is in the range of 0.1 to 0.3 wt%.
[0026]
【The invention's effect】
As described above, the brazing material of the present invention contains B 2 , Si, and C, and the balance is Fe, so that the melting point can be lowered to enable brazing. Furthermore , by containing Ni, Cr, or Mo in an appropriate range, hardenability can be improved and temper embrittlement can be mitigated. That is, in the standard state, a tempered martensite structure can be obtained by tempering after quenching or normalizing treatment, as in the case of structural alloys, although it has the same ferrite-pearlite structure as the structural alloy. It became possible to improve the Charpy impact value.
[Brief description of the drawings]
FIG. 1 is a schematic diagram showing a cross-sectional structure of a base material and a brazing material part joined using a brazing material of the present invention.
FIG. 2 is a schematic diagram showing a cross-sectional structure of a base material and a brazing material part joined using a brazing material of the prior art.
Claims (6)
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