JPH01273693A - Build-up welding material - Google Patents
Build-up welding materialInfo
- Publication number
- JPH01273693A JPH01273693A JP10323488A JP10323488A JPH01273693A JP H01273693 A JPH01273693 A JP H01273693A JP 10323488 A JP10323488 A JP 10323488A JP 10323488 A JP10323488 A JP 10323488A JP H01273693 A JPH01273693 A JP H01273693A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- less
- welding material
- corrosion resistance
- hardness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000003466 welding Methods 0.000 title claims abstract description 45
- 239000000463 material Substances 0.000 title claims abstract description 27
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 16
- 239000000956 alloy Substances 0.000 claims abstract description 16
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract 4
- 238000005552 hardfacing Methods 0.000 claims 1
- 230000007797 corrosion Effects 0.000 abstract description 33
- 238000005260 corrosion Methods 0.000 abstract description 33
- 239000000843 powder Substances 0.000 abstract description 15
- 239000000295 fuel oil Substances 0.000 abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 abstract description 6
- 238000002485 combustion reaction Methods 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 10
- 230000000694 effects Effects 0.000 description 10
- 238000005336 cracking Methods 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 229910001347 Stellite Inorganic materials 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- AHICWQREWHDHHF-UHFFFAOYSA-N chromium;cobalt;iron;manganese;methane;molybdenum;nickel;silicon;tungsten Chemical compound C.[Si].[Cr].[Mn].[Fe].[Co].[Ni].[Mo].[W] AHICWQREWHDHHF-UHFFFAOYSA-N 0.000 description 4
- 239000000446 fuel Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 239000007789 gas Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- 229910018487 Ni—Cr Inorganic materials 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- 238000009689 gas atomisation Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 238000003475 lamination Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000002893 slag Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910000521 B alloy Inorganic materials 0.000 description 1
- -1 C: 0.01 to 0.50% Inorganic materials 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910001080 W alloy Inorganic materials 0.000 description 1
- LNSPFAOULBTYBI-UHFFFAOYSA-N [O].C#C Chemical group [O].C#C LNSPFAOULBTYBI-UHFFFAOYSA-N 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000000567 combustion gas Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000010112 shell-mould casting Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- 238000009692 water atomization Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3033—Ni as the principal constituent
- B23K35/304—Ni as the principal constituent with Cr as the next major constituent
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
Description
（産業上の利用分野）
本発明は、肉盛溶接材料に係り、より詳しくは、耐熱、
耐食、耐摩耗肉盛に使用される溶接材料に関するもので
、主としてディーゼルエンジン用バルブ、ボイラーチュ
ーブ等の肉盛に適する。
（従来の技術）
内燃機のエンジンバルブ、バルブシートは高温の燃焼ガ
スに曝され、高温での金属間摩耗も受ける部品であるこ
とから、摩耗を受ける部分に肉盛溶接して用いることが
多い。
従来より、耐熱、耐食、耐摩耗用の肉盛材料としてはＣ
ｏ−Ｃｒ−Ｗ合金（ステライト合金）やＮｉ−Ｃｒ−８
ｉ−Ｂ合金（コルモノイ合金）がよく知られている。こ
れらの合金は高温における硬度が高く、耐食性も良好で
あり、更には溶接性にも優れていることから、エンジン
バルブへの肉盛に多用されている。
（発明が解決しようとする課題）
燃料としてガソリンを用いるエンジンのバルブについて
は、これらの肉感材料で特に問題はなく、良好な性能が
得られている。しかし、重油を燃料とするディーゼルエ
ンジン（特に船舶用エンジン）においては、最近の使用
環境の変化により、従来のステライト合金やコルモノイ
合金では十分な性能が得られなくなっている。
すなわち、重油には、不純物としてＶ（バナジウム）や
Ｓ（イオウ）が含まれており、これらは高温時において
極めて強い腐食性を示す成分である。
良質な重油を用いている場合は、ＶやＳが少ないため、
バルブ等の腐食もあまり問題とならないが。
近年、燃料費削減のため、低質重油の使用が増加してき
ており、低質重油にはこれらの成分が多く含まれている
ため、従来の肉盛材料では耐食性が不十分でバルブ寿命
の低下を来たしている。
このため、低質重油に対する耐食性の向上を図る対策と
して、従来より、ｖ、Ｓ腐食にはＮ１−Ｃｒ（２０％以
上）系合金が有用であることが知られており、ボイラー
チューブへの溶射等では一部使用されている。しかし、
通常のＮｉ−Ｃｒ合金は硬さが低く、耐摩耗性が不十分
でエンジンバルブへ適用することは困難である。
また、特開昭５６−８４１９３号にみられるように、Ｎ
ｉ−Ｃｒ合金を改良して熱処理により硬さを得ることも
試みられているが、熱処理温度として８００’Ｃ以上が
必要であり、これでは一般に用いられる母材は劣化する
ため、実用上大きな制約となっている。
本発明は、上記従来技術の問題点を解決し、高温におい
て十分な酎Ｖ、耐Ｓ腐食性と耐摩耗性を兼ね備え得る硬
質肉盛溶接材料を提供することを目的とするものである
。
ＣＲＭを解決するための手段）
前記目的を達成するため、本発明者等は、溶接後に特別
の熱処理を必要とせずに所期の性質を具備し得るＮｉ基
合金を見い出すべく、その成分組成について鋭意研究を
重ねた。その結果、特定の種々の元素の含有量をバラン
スよく調整することにより、可能であることが判明し、
ここに本発明をなしたのである。
すなわち、本発明に係る硬質肉盛溶接材料は、Ｎｉ基合
金であッテ、Ｃ：０．０１〜０．５０％、Ｓｉ：０．１
〜２．０％、Ｃｒ：３５〜６０％、Ａｆｌ＋Ｔｉ：０．
５〜４．０（但し、Ｔｉのみの場合は０．５〜３．０％
）及びＮ：０．０１〜０．２％を含み、更に、Ｍｎ：２
％以下、ｖ：３％以下、Ｎｂ：１％以下、Ｍｏ：５％以
下、Ｗ：５％以下及びＦｅ：５％以下のうちの１種又は
２種以上を含み、残部がＮ１或いはＮｉと３０％以下の
Ｃｏ並びに不可避的不純物からなることを特徴とするも
のである。
以下に本発明を更に詳細に説明する。
（作用）
本発明における化学成分の限定理由は次のとおりである
。
Ｃ：
Ｃは固溶体を強化する成分である。しかし、０゜０１％
より少ないと十分な硬さを得ることができず、また０、
５０％を超えると溶接時に割れを発生する。したがって
、Ｃ量は０．０１〜０．５０％の範囲とする。
Ｓｉ：
Ｓｉは作業性を安定させるために必要な成分である。し
かし、０．１％以下では母材とのなじみが悪く、一方、
２．０％を超えると渦流れがよくなりすぎて溶着不良を
発生する。したがって、Ｓｉ量は０．１〜２．０％の範
囲とする。
Ｃｒ：
耐食、耐熱性を得るために必要な成分であり、３５％以
上で効果がある。３５％未満では耐熱性が不十分で、酸
化し易くなり、耐食性も劣化する。
また６５％を超えると急速に脆化して、溶着金属は極め
て割れ易くなる。したがって、Ｃｒ量は３５〜６０％の
範囲とする。
Ａｌ、Ｔｉ：
ＡｌはＮｉと金属間化合物を形成して硬さを得る成分で
ある。しかし、０．５％未満では十分な硬さが得られな
い。また、Ａｌ２は溶接棒を製造する場合の鋳造性を改
良する成分でもある。Ｎ ｉ −Ｃｒ系は鋳造性の悪い
材料で細径の溶接棒の製造が難しいが、これに八〇を０
．５％以上添加すると良好な鋳造が可能となる。Ａｌ１
が４％以上になると逆に酸化物が多くなり、鋳造性を阻
害するため、Ａｌ量は０．５〜４．０％が適当である。
なお、Ａ２の一部又は全部をＴｉと等量で置き換えるこ
とが可能であるが、Ｔｉのみの場合は。
３．０％を超えると耐ブローホール性を悪くするので、
その添加量は３．０％以下に抑える必要がある。
したがって、Ａｌのみの添加のときのＡｌ量及びＡｌ＋
Ｔｉの量は０．５〜４．０％の範囲とし、Ｔｉのみの添
加のときのＴｉ量は０．５〜３．０の範囲とする。
Ｎ：
ＮはＣｒと窒化物を形成して硬さを安定させる効果があ
る。しかし、０．０１％未満ではこの効果が得られず、
また０、２％を超えると溶湯の流動性が悪くなり、鋳造
性を阻害する。したがって。
Ｎ量は０．０１〜０．２％の範囲とする。
上記各成分に加えて、硬さをより安定とするために次の
成分のうちの少なくとも１種の添加が必要である。
Ｎｂ：
Ｎｂは１％以下の添加により、高温硬さを安定にする効
果があるが、１％を超えると鋳造性を阻害すると共に脆
化するので好ましくない。
Ｍｎ：
Ｍｎは固溶体を強化して常温での硬さを安定とし１作業
性も良くする（主としてなじみ）が、２％を超える量を
添加するとスラグ発生量が多くなるので好ましくない。
Ｗ：
ＷはＭｎと同様の効果があるが、作業性には寄与しない
、添加量は５％までは効果が認められる。
しかし、５％を超えると溶接金属の耐割れ性を悪くする
ので好ましくない。
Ｆｅ：
Ｆｅは硬さを若干高くする作用があり、また鋳造性を良
くする成分である。但し、耐食性を悪くする成分でもあ
るため、添加量は５％以下とすべきである。
■＝
■は３％以下の添加で５００℃までの高温硬さを安定に
する効果がある。しかし、３％を超えると耐割れ性を阻
害するので好ましくない。
Ｍｏ：
ＭｏはＷと同様の効果がある。しかし、５％を超えると
溶接金属の耐割れ性を悪くするので、５％以下とする。
なお−Ｍｏは当量のＷと置換しても同様の効果がある。
なお、本発明はＮｉ基合金であり、残部はＮｉ及び不可
避的不純物からなるが、Ｎｉの一部をＣｏに置き換えて
も基本特性は同様のものが得られる。
但し、Ｃｏが３０％を超えると硬さが低下するため、Ｎ
ｉをＣＯに置換する場合は３０％以下とする。
不可避的不純物としての酸素は５００ｐｐｍ、水素は１
８０ｐｐｍ以下に抑えることが望ましい、それぞれこの
値を超えるとブローホール等の増加傾向がみられ、特に
本溶接材料を粉末プラズマ溶接用として用いた場合に融
合不良が発生し易くなる。
以上の成分を有する溶接材料は、主としてＴＩＧ溶接溶
接粉末溶接材料として提供される。
ＴＩＧ溶接溶接粉る場合は、一般に鋳造法で製造するの
が良い、鋳造方法としてはシェルモールド法、減圧吸引
法、連続鋳造法等があり、細径棒を鋳造できる方法であ
ればどのような方法によっても良い。溶接棒径としては
、溶接作業性、経済性の各面より一般に３．２〜６．０
＋ａｍφが実用的である。なお、本溶接材料にはＡＲ，
Ｔｉが含まれているので、酸素−アセチレンガス溶接は
困難である。
粉末材料として提供する場合は粉体プラズマ溶接用とし
て用いるのが好ましい、粉末としては６０〜３５０メツ
シュ程度とすることが良好な溶接作業性を確保するため
に望ましい、粉末の製造方法はガスアトマイズ法による
ものが最も適している。勿論、水アトマイズ法により製
造することも可能であるが、ガス成分が多くなりやすく
、特に酸素を低く抑えるのが難しく、溶接材料の製法と
してあまり好ましくない。
本発明による溶接材料はディーゼルエンジンバルブ以外
にも重油を燃料として用いる機器の耐食、耐摩耗肉感に
広く利用できることは云うまでもない。
（実施例）
次に本発明の実施例を示す。
実施例１
本例は溶接棒として利用した例である。
第１表に示す化学成分を有する溶接棒を用い、以下の溶
接条件のＴＩＧ溶接により肉盛溶接した。
作業性及び割れ状況を調べると共に耐食テスト及び硬さ
測定を行った結果を第２表に示す。
〈溶接条件〉
溶接棒径：５．０φ鋳造棒
電流： １５０Ａ（ＤＣ８Ｐ）
予熱温度：２．００℃
母材：５Ｍ５０Ａ
１９ｔＸ１００Ｘ２００ｕ（＋ｎ＋ａ）積層法：２層盛
（３パス／１層）
シールドガス：Ａｌ １５Ｑ／ｗｉｎなお、耐食試験
方法には、３ｔＸ １０ｗＸ４０ Ｑ（ｍｍ）の寸法の
試験片を用い、耐Ｖ腐食の評価の場合は、Ｖ、Ｏ，％＋
Ｎａ、 Ｓ ０．１５％の腐食溶液を２０ Ｂ／ｃｍ”
塗布し、９００℃Ｘ３ｈｒ（大気）に加熱して腐食減量
を測定し、また耐Ｓ腐食の評価の場合は、前記腐食溶液
をＮａ、３０．９０％＋ＮａＣＱ１０％に代えた以外は
同じ条件で塗布、加熱し。
腐食減量を測定した。
第２表より以下の如く考察される。
Ｎα１〜Ｎａ ５は本発明例であって、良好な作業性を
示し、割れのない溶着金属が得られた。また耐食性も良
好で、耐Ｖ腐食２０ｍｇ／ａｍ２以下、耐Ｓ腐食５ｍｇ
／Ｃｍ以下となり、ステライトやコルモノイに比べて良
好な値を示している。また硬さもＩ−Ｉｖ４００以上が
得られ、十分な耐摩耗性が期待できる。
一方、比較例Ｎα６はＣが低いため、硬さがＨｖ３２０
と低く、更にＦｅ量が多いため、耐食性が悪い。
比較例Ｎα７はＭｎが多いのでスラグを発生し、作業性
が悪い、更にＡｆｌとＴｉが不足しているため、硬さは
低くなっている。
比較例Ｎα８はＣｒが不足して耐食性不良であり、低Ｓ
Ｌによるなじみ不良も起こっている。更にＮｂが高すぎ
るため、割れが発生している。
比較例Ｎα９はＣが多すぎるため、割れを発生している
。
比較例Ｎｎ１ＯはＳｉが高すぎてコールドラップとなり
、高Ｃｒによる割れも発生している。
比較例Ｎ（１１１はＴｉが多すぎてブローホールを発生
し、Ｗも多すぎて割れを発生している。
比較例Ｎα１２は高Ａｌで割れを発生している。
比較例Ｎｎ１３はＡｌが低すぎて硬さがです、高Ｎによ
りなじみが悪くなっている。また■が高すぎて割れを発
生している。
比較例ＮＱ１４はステライト合金であり、作業性、硬さ
は問題ないが、耐食性が悪い。
比較例ＮＱ１５はコルモノイ合金であり、作業性１
は良いが、２００℃予熱では割れを発生している。
耐食性も不十分である。
［以下余白１
ス」１１Ａ
本例は粉体プラズマ溶接の粉末として利用した例である
。
第３表に示す化学成分を有する粉末をガスアトマイズ法
により製造し、これを用いて以下の溶接条件の粉体プラ
ズマ肉盛溶接を行った。
く溶接条件〉
母 材：ＳＣＭ４４５
１９ｔＸ１００ｗＸ３００Ｑ（ｍｍ）
電 流：１６０Ａ ＤＣ３Ｐ
予熱温度：２００℃
積層法：２層法（３バス／１層）
その結果、Ｎａ １、Ｎａ２は作業性が特に良好で。
割れのない施工ができた。一方、Ｎａ３は粒度が粗いた
め、粉末が若干溶けに＜＜、融合がやや不足気味となる
傾向がみられた。また、＆４は逆に粒度が細かすぎて粉
末の飛散が若干多くなり、ノズルがやや詰まり易くなる
傾向が生じた。しかし。
いずれの場合も、実施例１の本発明例と同様１割れがな
く、■腐食及びＳ腐食に対する耐食性が優れ、硬さも十
分であった。(Industrial Application Field) The present invention relates to overlay welding materials, and more specifically, heat-resistant,
This relates to welding materials used for corrosion-resistant and wear-resistant overlays, and is mainly suitable for overlaying diesel engine valves, boiler tubes, etc. (Prior Art) Engine valves and valve seats of internal combustion engines are parts that are exposed to high-temperature combustion gas and also undergo metal-to-metal wear at high temperatures, so they are often used by overlay welding on the parts that are subject to wear. Traditionally, C has been used as a build-up material for heat resistance, corrosion resistance, and wear resistance.
o-Cr-W alloy (stellite alloy) and Ni-Cr-8
The i-B alloy (Colmonoy alloy) is well known. These alloys have high hardness at high temperatures, good corrosion resistance, and excellent weldability, so they are often used for overlaying engine valves. (Problems to be Solved by the Invention) Regarding the valves of engines that use gasoline as fuel, there are no particular problems with these sensuous materials, and good performance has been obtained. However, in diesel engines (particularly marine engines) that use heavy oil as fuel, due to recent changes in the usage environment, it is no longer possible to obtain sufficient performance with conventional stellite alloys and colmonoy alloys. That is, heavy oil contains V (vanadium) and S (sulfur) as impurities, and these are components that exhibit extremely strong corrosive properties at high temperatures. When using high quality heavy oil, V and S are low, so
Corrosion of valves, etc. is not much of a problem. In recent years, the use of low-quality heavy oil has increased in order to reduce fuel costs.As low-quality heavy oil contains many of these components, conventional overlay materials have insufficient corrosion resistance and shorten valve life. ing. Therefore, as a measure to improve corrosion resistance against low-quality heavy oil, it has been known that N1-Cr (20% or more) alloys are effective against V and S corrosion, and thermal spraying on boiler tubes, etc. It is partially used. but,
Ordinary Ni-Cr alloys have low hardness and insufficient wear resistance, making it difficult to apply them to engine valves. Also, as seen in Japanese Patent Application Laid-Open No. 56-84193, N
Attempts have been made to improve the i-Cr alloy and obtain hardness through heat treatment, but this requires a heat treatment temperature of 800'C or higher, which deteriorates the commonly used base material, which poses a major practical limitation. It becomes. The object of the present invention is to solve the problems of the above-mentioned prior art and to provide a hard overlay welding material that can have sufficient corrosion resistance and wear resistance at high temperatures. Means for Solving CRM) In order to achieve the above object, the present inventors investigated the composition of Ni-based alloys in order to find a Ni-based alloy that can have the desired properties without requiring special heat treatment after welding. I have done extensive research. As a result, it was found that it is possible to achieve this by adjusting the content of various specific elements in a well-balanced manner.
This is where the present invention was made. That is, the hard overlay welding material according to the present invention is a Ni-based alloy, C: 0.01 to 0.50%, Si: 0.1
~2.0%, Cr: 35-60%, Afl+Ti: 0.
5 to 4.0 (however, in the case of Ti only, 0.5 to 3.0%
) and N: 0.01 to 0.2%, and further contains Mn: 2
% or less, v: 3% or less, Nb: 1% or less, Mo: 5% or less, W: 5% or less, and Fe: 5% or less, and the balance is N1 or Ni. It is characterized by comprising 30% or less of Co and unavoidable impurities. The present invention will be explained in more detail below. (Function) The reasons for limiting the chemical components in the present invention are as follows. C: C is a component that strengthens the solid solution. However, 0°01%
If it is less, sufficient hardness cannot be obtained, and if it is less than 0,
If it exceeds 50%, cracks will occur during welding. Therefore, the amount of C is set in the range of 0.01 to 0.50%. Si: Si is a necessary component to stabilize workability. However, if it is less than 0.1%, the compatibility with the base material is poor;
If it exceeds 2.0%, vortex flow becomes too strong, resulting in poor welding. Therefore, the amount of Si is set in the range of 0.1 to 2.0%. Cr: A necessary component to obtain corrosion resistance and heat resistance, and is effective at 35% or more. If it is less than 35%, heat resistance will be insufficient, oxidation will easily occur, and corrosion resistance will also deteriorate. Moreover, if it exceeds 65%, it will rapidly become brittle and the welded metal will become extremely susceptible to cracking. Therefore, the Cr content is set in the range of 35 to 60%. Al, Ti: Al is a component that forms an intermetallic compound with Ni to obtain hardness. However, if it is less than 0.5%, sufficient hardness cannot be obtained. Furthermore, Al2 is also a component that improves castability when manufacturing welding rods. Ni-Cr is a material with poor castability and it is difficult to manufacture small diameter welding rods.
．． Adding 5% or more enables good casting. Al1
If the Al content exceeds 4%, the amount of oxide increases and the castability is impaired, so the appropriate Al content is 0.5 to 4.0%. Note that it is possible to replace part or all of A2 with an equal amount of Ti, but in the case of using only Ti. If it exceeds 3.0%, the blowhole resistance will deteriorate, so
The amount added needs to be suppressed to 3.0% or less. Therefore, the amount of Al and Al+ when only Al is added
The amount of Ti is in the range of 0.5 to 4.0%, and when only Ti is added, the amount of Ti is in the range of 0.5 to 3.0. N: N forms a nitride with Cr and has the effect of stabilizing hardness. However, if it is less than 0.01%, this effect cannot be obtained,
Moreover, if it exceeds 0.2%, the fluidity of the molten metal deteriorates, inhibiting castability. therefore. The amount of N is in the range of 0.01 to 0.2%. In addition to the above components, it is necessary to add at least one of the following components to make the hardness more stable. Nb: Nb has the effect of stabilizing high-temperature hardness when added in an amount of 1% or less, but if it exceeds 1%, it impairs castability and causes embrittlement, which is not preferable. Mn: Mn strengthens the solid solution, stabilizes the hardness at room temperature, and improves workability (mainly due to break-in), but if it is added in an amount exceeding 2%, the amount of slag generated increases, which is not preferable. W: W has the same effect as Mn, but does not contribute to workability, and is effective up to 5%. However, if it exceeds 5%, it is not preferable because it deteriorates the cracking resistance of the weld metal. Fe: Fe has the effect of slightly increasing hardness and is a component that improves castability. However, since it is a component that worsens corrosion resistance, the amount added should be 5% or less. ■= ■ Addition of 3% or less has the effect of stabilizing high-temperature hardness up to 500°C. However, if it exceeds 3%, cracking resistance will be impaired, which is not preferable. Mo: Mo has the same effect as W. However, if it exceeds 5%, the cracking resistance of the weld metal deteriorates, so the content should be 5% or less. Note that even if -Mo is replaced with an equivalent amount of W, the same effect can be obtained. Note that although the present invention is a Ni-based alloy, and the remainder consists of Ni and unavoidable impurities, the same basic characteristics can be obtained even if a part of Ni is replaced with Co. However, if Co exceeds 30%, the hardness decreases, so N
When replacing i with CO, the content should be 30% or less. Oxygen as an unavoidable impurity is 500 ppm, hydrogen is 1
It is desirable to suppress the content to 80 ppm or less; if this value is exceeded, blowholes and the like tend to increase, and poor fusion tends to occur particularly when the present welding material is used for powder plasma welding. Welding materials having the above components are mainly provided as TIG welding powder welding materials. When producing TIG welding powder, it is generally best to manufacture it by casting. Examples of casting methods include shell molding, vacuum suction, and continuous casting. It depends on the method. The diameter of the welding rod is generally 3.2 to 6.0 from the viewpoint of welding workability and economy.
+amφ is practical. In addition, this welding material includes AR,
Oxygen-acetylene gas welding is difficult because of the Ti content. When provided as a powder material, it is preferable to use it for powder plasma welding.As a powder, it is desirable to have a mesh size of about 60 to 350 to ensure good welding workability.The method of manufacturing the powder is by gas atomization. is most suitable. Of course, it is also possible to manufacture by water atomization, but the gas components tend to increase, and it is particularly difficult to keep oxygen to a low level, so this is not a very preferable method for manufacturing welding materials. It goes without saying that the welding material of the present invention can be widely used for corrosion and wear resistance of equipment that uses heavy oil as fuel, in addition to diesel engine valves. (Example) Next, an example of the present invention will be shown. Example 1 This example is an example of use as a welding rod. Overlay welding was performed by TIG welding under the following welding conditions using a welding rod having the chemical composition shown in Table 1. Table 2 shows the results of examining workability and cracking conditions, as well as corrosion resistance tests and hardness measurements. <Welding conditions> Welding rod diameter: 5.0φ Casting rod Current: 150A (DC8P) Preheating temperature: 2.00℃ Base material: 5M50A 19tX100X200u (+n+a) Lamination method: 2 layers (3 passes/1 layer) Shielding gas: Al 15Q/winThe corrosion resistance test method uses a test piece with dimensions of 3tX 10wX40Q (mm), and in the case of evaluating V corrosion resistance, V, O,%+
Na, S 0.15% corrosion solution at 20 B/cm”
The corrosion loss was measured by heating at 900°C for 3 hr (atmosphere), and for the evaluation of S corrosion resistance, the coating was applied under the same conditions except that the corrosion solution was replaced with Na, 30.90% + NaCQ 10%. , heated. Corrosion loss was measured. The following considerations can be made from Table 2. Nα1 to Na5 are examples of the present invention, and exhibited good workability, and welded metals without cracks were obtained. It also has good corrosion resistance, with V corrosion resistance of 20 mg/am2 or less and S corrosion resistance of 5 mg.
/Cm or less, which is a better value than stellite and colmonoy. Further, a hardness of I-Iv400 or higher can be obtained, and sufficient wear resistance can be expected. On the other hand, because the comparative example Nα6 has a low C content, its hardness is Hv320.
Furthermore, since the amount of Fe is large, the corrosion resistance is poor. Comparative Example Nα7 has a large amount of Mn, so it generates slag, resulting in poor workability.Furthermore, it lacks Afl and Ti, so its hardness is low. Comparative example Nα8 lacks Cr, has poor corrosion resistance, and has low S
Poor compatibility due to L also occurs. Furthermore, cracks occur because the Nb content is too high. Comparative Example Nα9 has too much C, so cracks occur. In Comparative Example Nn1O, the Si content was too high, resulting in cold lap, and cracks also occurred due to the high Cr content. Comparative example N (111 has too much Ti, which causes blowholes, and too much W, which causes cracks. Comparative example Nα12 has a high Al content, which causes cracks. Comparative example Nn13 has a low Al content. The hardness is too high, and the conformability is poor due to the high N. Also, the ■ is too high, causing cracks.Comparative example NQ14 is a stellite alloy, and there are no problems in workability and hardness, but the corrosion resistance is poor. Comparative example NQ15 is a Colmonoy alloy and has workability of 1.
Although the temperature was good, cracking occurred when preheating to 200°C. Corrosion resistance is also insufficient. [1 space below] 11A This example is an example in which the powder is used as a powder for powder plasma welding. Powders having the chemical components shown in Table 3 were produced by a gas atomization method, and were used to perform powder plasma overlay welding under the following welding conditions. Welding conditions> Base material: SCM445 19tX100wX300Q (mm) Current: 160A DC3P Preheating temperature: 200℃ Lamination method: 2 layer method (3 baths/1 layer) As a result, Na 1 and Na 2 have particularly good workability. Construction was completed without cracking. On the other hand, since the particle size of Na3 was coarse, there was a tendency for the powder to dissolve slightly<< and for fusion to be slightly insufficient. On the other hand, &4 had a particle size that was too fine, resulting in slightly more powder scattering, and a tendency for the nozzle to become slightly clogged. but. In any case, there was no single crack as in the invention example of Example 1, and the corrosion resistance against (1) corrosion and S corrosion was excellent, and the hardness was also sufficient.
（発明の効果）
以上詳述したように、本発明によれば、Ｎｉ基合金の化
学成分をバランスよく調整したので、耐熱性、耐摩耗性
は勿論のこと、特に高温における耐Ｖ、耐Ｓ腐食性に優
れた肉盛溶接材料を提供することができる。しかも、溶
着金属に特別の熱処理を要することなく特性を得ること
ができるので、実用上の効果は大きい。特にｖ、Ｓを含
む低質重油を使用する環境に曝される各種機器、部品の
肉 ゛盛溶接材料として好適である。
特許出願人 株式会社神戸製鋼所
代理人弁理士 中 村 尚(Effects of the Invention) As detailed above, according to the present invention, the chemical components of the Ni-based alloy are adjusted in a well-balanced manner. It is possible to provide an overlay welding material with excellent corrosion resistance. Moreover, since the properties can be obtained without requiring special heat treatment of the weld metal, the practical effect is great. In particular, it is suitable as an overlay welding material for various equipment and parts that are exposed to environments where low-quality heavy oil containing V and S is used. Patent applicant Hisashi Nakamura, patent attorney representing Kobe Steel, Ltd.
Claims (1)
．０１〜０．５０％、Ｓｉ：０．１〜２．０％、Ｃｒ：
３５〜６０％、Ａｌ＋Ｔｉ：０．５〜４．０％（但し、
Ｔｉのみの場合は０．５〜３．０％）及びＮ：０．０１
〜０．２％を含み、更に、Ｍｎ：２％以下、Ｖ：３％以
下、Ｎｂ：１％以下、Ｍｏ：５％以下、Ｗ：５％以下及
びＦｅ：５％以下のうちの１種又は２種以上を含み、残
部がＮｉ或いはＮｉと３０％以下のＣｏ並びに不可避的
不純物からなることを特徴とする硬化肉盛溶接材料。Ni-based alloy, in weight% (hereinafter the same), C: 0
．． 01-0.50%, Si: 0.1-2.0%, Cr:
35-60%, Al+Ti: 0.5-4.0% (however,
0.5-3.0% in case of Ti only) and N: 0.01
~0.2%, and further one of Mn: 2% or less, V: 3% or less, Nb: 1% or less, Mo: 5% or less, W: 5% or less, and Fe: 5% or less. or a hardfacing welding material comprising two or more of these, the remainder being Ni or Ni and 30% or less of Co and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10323488A JPH01273693A (en) | 1988-04-25 | 1988-04-25 | Build-up welding material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10323488A JPH01273693A (en) | 1988-04-25 | 1988-04-25 | Build-up welding material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01273693A true JPH01273693A (en) | 1989-11-01 |
Family
ID=14348763
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10323488A Pending JPH01273693A (en) | 1988-04-25 | 1988-04-25 | Build-up welding material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01273693A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1996017098A1 (en) * | 1994-12-02 | 1996-06-06 | Toyota Jidosha Kabushiki Kaisha | High-chromium nickel alloy with excellent resistances to wear and lead corrosion and engine valve |
| EP3915717A1 (en) | 2020-05-26 | 2021-12-01 | Daido Steel Co., Ltd. | Ni-based alloy, and ni-based alloy product and methods for producing the same |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6233089A (en) * | 1985-08-02 | 1987-02-13 | Daido Steel Co Ltd | Alloy powder for building up of powder |
-
1988
- 1988-04-25 JP JP10323488A patent/JPH01273693A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6233089A (en) * | 1985-08-02 | 1987-02-13 | Daido Steel Co Ltd | Alloy powder for building up of powder |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1996017098A1 (en) * | 1994-12-02 | 1996-06-06 | Toyota Jidosha Kabushiki Kaisha | High-chromium nickel alloy with excellent resistances to wear and lead corrosion and engine valve |
| EP3915717A1 (en) | 2020-05-26 | 2021-12-01 | Daido Steel Co., Ltd. | Ni-based alloy, and ni-based alloy product and methods for producing the same |
| US11732331B2 (en) | 2020-05-26 | 2023-08-22 | Daido Steel Co., Ltd. | Ni-based alloy, and Ni-based alloy product and methods for producing the same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5486093B2 (en) | Wear-resistant cobalt base alloy and engine valve | |
| JP5742447B2 (en) | High hardness overlaying alloy powder | |
| US20120267420A1 (en) | Fine grained ni-based alloys for resistance to stress corrosion cracking and methods for their design | |
| JP5486092B2 (en) | High toughness cobalt base alloy and engine valve | |
| CA2491754C (en) | Wear-resistant, corrosion-resistant cobalt-based alloys | |
| JPS586779B2 (en) | Wear-resistant iron-nickel-cobalt alloy | |
| US5422071A (en) | Heat resistant iron/steel weld material | |
| CN112192090B (en) | Chromium carbide enhanced nickel-aluminum-based flux-cored wire for hardfacing and preparation method thereof | |
| JP6156316B2 (en) | Overlaying alloy powder, overlaying alloy member using the same, and engine valve | |
| CN109454357A (en) | A kind of nickel-base welding rod and preparation method thereof | |
| US20040011435A1 (en) | Wear-resistant, corrosion-resistant cobalt-based alloys | |
| JP2014111265A (en) | Cladding powder alloy | |
| US2783144A (en) | Hard facing alloy | |
| JPH01273693A (en) | Build-up welding material | |
| JPH055599B2 (en) | ||
| JP2019157176A (en) | Copper-based alloy | |
| JPS5940212B2 (en) | Co-based alloy for engine valves and valve seats of internal combustion engines | |
| JP2673593B2 (en) | Built-in engine valve for intake | |
| JPS62179891A (en) | Ni welding material for hard facing | |
| JP3855257B2 (en) | Cr-Ni-Nb-Fe base alloy for overlaying | |
| JPS61113742A (en) | High-hardness heat-resistant alloy | |
| JPS5970744A (en) | High-hardness ni alloy for valve and valve seat for engine | |
| JP3332771B2 (en) | Corrosion and heat resistant Ni-base casting alloy for waste incinerator | |
| JPH02205294A (en) | Overplaying alloy having excellent high-temperature tensile creep characteristic | |
| JPS62156095A (en) | Ni-base high toughness heat resisting alloy for hard facing |