JPH0532158B2 - - Google Patents
Info
- Publication number
- JPH0532158B2 JPH0532158B2 JP60171606A JP17160685A JPH0532158B2 JP H0532158 B2 JPH0532158 B2 JP H0532158B2 JP 60171606 A JP60171606 A JP 60171606A JP 17160685 A JP17160685 A JP 17160685A JP H0532158 B2 JPH0532158 B2 JP H0532158B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- less
- overlay
- based alloy
- alloy powder
- 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.)
- Expired - Lifetime
Links
- 239000000843 powder Substances 0.000 claims description 104
- 239000000956 alloy Substances 0.000 claims description 53
- 229910045601 alloy Inorganic materials 0.000 claims description 53
- 229910052760 oxygen Inorganic materials 0.000 claims description 29
- 239000001301 oxygen Substances 0.000 claims description 25
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 23
- 239000007789 gas Substances 0.000 claims description 19
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 229910052715 tantalum Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 description 25
- 229910052751 metal Inorganic materials 0.000 description 25
- 238000000034 method Methods 0.000 description 25
- 238000003466 welding Methods 0.000 description 18
- 239000011324 bead Substances 0.000 description 12
- 238000001816 cooling Methods 0.000 description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 8
- 238000009689 gas atomisation Methods 0.000 description 7
- 230000007547 defect Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 239000000758 substrate Substances 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000010298 pulverizing process Methods 0.000 description 3
- 238000005507 spraying Methods 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000945 filler Substances 0.000 description 2
- 230000001788 irregular Effects 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 1
- 238000011276 addition treatment Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- QFXZANXYUCUTQH-UHFFFAOYSA-N ethynol Chemical group OC#C QFXZANXYUCUTQH-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Description
［発明の目的］
（産業上の利用分野）
本発明は、粉末肉盛溶接に利用される粉末肉盛
用Co基合金粉末に関するものである。
（従来の技術）
基体の表面に耐食・耐熱性あるいは耐摩耗性等
を付与し、または基体表面の前記特性をさらに向
上させるために、肉盛溶接（Surfacing）を行う
ことが多い。
この肉盛溶接法としては、種々のものが開発さ
れているが、とくに粉末を溶加材としかつプラズ
マアークを熱源とする粉末肉盛溶接法は、溶加棒
を用いる酸素アセチレン溶接法、TIG溶接法など
に比較して、高速でかつ自動化しやすいことか
ら、近年とくに注目を集めるようになつている。
この粉末肉盛溶接において使用される合金粉末
は、溶融合金に対してガス噴霧を行つたのちガ
ス中で冷却する方法、溶融合金に対してガス噴
霧を行つたのち液（水）中で冷却する方法、溶
融合金に対して液（水）噴霧を行う方法、溶融
合金に対して遠心力を加える方法、溶融合金を
高速回転するロールの隙間に流下させる方法、な
どによつて製造される。
このような粉末製造法において、溶融合金がア
トマイジングによつて粉化したのちの冷却速度が
小さいときには、溶融粉体の表面張力によつて球
状化するが、冷却速度が大きいときには、溶融粉
体が球状化する以前に凝固してしまうので、不規
則形状の粉末となる。
（発明が解決しようとする問題点）
ところで、上記した不規則形状の粉末は、その
長短比が大きく、かつ一定していないものである
ため、この粉末を粉末肉盛用の粉末として用いた
場合には、当該粉末の送給性が劣ることとなる。
そのため、従来においては、粉末の送給機構に
種々の工夫がなされてきたが、それでも、粉末の
送給むらによるビード形状の不良、例えば、湯切
れ、肉盛金属のビード幅の不均一などの不良が発
生しやすいという問題点があつた。
一方、冷却速度の小さいガス噴霧法により製造
した粉末は、その長短比が小さい球形状をなすた
め、粉末の送給性が良好であり、したがつてビー
ド形状も良好なものとなる。
しかしながら、ビード形状は良好となるもの
の、肉盛金属内にブローホールを生ずることがあ
るという問題点があつた。
本発明は、上述した従来の問題点に着目してな
されたもので、粉末の送給性に優れているため、
湯切れやビード幅の不均一などの不具合が発生せ
ず、ビード形状が良好であると同時に、肉盛金属
中にブローホールが発生しない粉末肉盛溶接を行
うことが可能である粉末肉盛用Co基合金粉末を
提供することを目的としている。
［発明の構成］
（問題点を解決するための手段）
本発明による粉末肉盛用合金粉末は、基体表面
の耐摩耗性、耐熱性、耐食性、耐薬品性等を高め
るために粉末肉盛溶接する際に使用されるCo基
合金粉末であつて、重量％で、Ｃ：0.05〜3.0％、
Si：5.0％以下、Mn：3.0％以下、Ｐ：0.03％以
下、Ｓ：0.03％以下、Cu：3.0％以下、Ni：30％
以下、Cr：10〜40％、Ｗ：20％以下、Mo：20％
以下、Ｂ：3.0％以下、Fe：５％以下、Ｎ：0.30
％以下、Ｏ：0.01〜0.50％、望ましくは、Ｏ：
0.02〜0.30％および場合によつては、さらにNb：
3.0％以下、Ta：3.0％以下、Ｖ：3.0％以下、
Zr：3.0％以下のうちの１種または２種以上を含
有し、残部Coおよび不純物よりなることを特徴
としている。
また、本発明による粉末肉盛用合金粉末の実施
態様においては、合金粉末の長短比が1.5以下で
あるものとすることが望ましく、また、前記合金
粉末は、噴霧ガス中の酸素量を調整して、Ｏ：
0.01〜0.50％としたものとすることができる。
本発明による粉末肉盛用合金粉末は、上述した
ように、酸素量が0.01重量％以上のものである
が、この理由は、粉末肉盛溶接後の肉盛金属中の
ブローホールをできるだけなくすためである。そ
して、肉盛金属中のブローホールをなくす観点か
らは粉末中の酸素量は0.50重量％以下とすれば十
分であり、より望ましくは0.02〜0.30重量％の範
囲とする。また、窒素量は0.30重量％以下とする
ことによつて肉盛金属中におけるブローホールの
発生を低減ないしは解消することが可能となる。
さらに、Ｃは炭化物を形成して硬さおよび高温
強度を高めるのに有効であるので、0.05％以上含
有させるが、多すぎると靱延性が低下するので、
3.0％以下とするのがよく、Siは肉盛金属中の非
金属介在物を減少させるので、5.0％以下の範囲
で添加するのがよく、Mnは肉盛金属の清浄度を
高めるので、3.0％以下の範囲で添加するのがよ
く、ＰおよびＳは肉盛金属の靱性を害するので、
いずれも0.03％以下に規制するのがよい。また、
Cuは強度を向上させるので3.0％までは添加して
もよく、Niは耐食性の向上に寄与するので30％
までは添加してもよい。さらに、Crは耐食性お
よび耐摩耗性を向上させるので、10％以上添加さ
せるのもよいが、多すぎると靱性が低下するの
で、40％以下とするのがよい。さらにまた、Ｗは
耐摩耗性を向上させるので20％まで添加してもよ
く、Moは耐食性および強度を増大させるので20
％までは添加してもよく、Ｂは強度を向上させる
ので3.0％までは添加してもよく、Feは肉盛金属
の特性を害することなく粉末のコストを低下させ
ることができるので５％以下までは添加してもよ
く、強度を向上させるためにNbを3.0％以下ま
で、Taを3.0％以下まで、Ｖを3.0％以下まで、Zr
を3.0％以下までそれぞれ添加してもよい。
本発明による粉末肉盛用合金粉末は、上記の成
分範囲をもつCo基合金からなるものであり、よ
り好適には長短比が1.5以下の球形状をなすもの
である。このような球形状をなす粉末は、粉化さ
れた溶融金属がその表面張力によつて球状化した
あと凝固する冷却速度を伴う製造手法、通常はガ
ス噴霧法が用いられる。
本発明による粉末肉盛用合金粉末は、Co基合
金粉末中において、酸素を0.01〜0.50％の範囲で
含有または付着させるとともに、Ｎ量を0.30％以
下に規制することによつて、肉盛金属内でブロー
ホールが発生するのを防ぐようにしたが、このよ
うな酸素量とするには、例えば、
Co基合金を溶製する際の溶融金属中の酸素
量を調整する方法、
噴霧ガス中の酸素量を調整する（必要に応じ
て噴霧ガスに酸素を添加する）方法、
噴霧雰囲気中の酸素量を調整する方法、
粉末を熱処理してその表面を酸化する方法、
粉末を酸洗してその表面を酸化する方法、
などがあり、これらの単独および組合わせによる
方法を採用することができる。また、そのほか、
高酸素粉末と低酸素粉末とを混合して粉末の
平均酸素量が0.01〜0.50％となるようにするこ
ともできる。
（実施例 １）
Co基合金を溶製したのち、このCo基合金溶湯
をN2ガスを使用したガス噴霧法により粉化し、
N2ガス中の酸素量が300〜1000ppmであるように
調整したチヤンバー内のガス雰囲気中で冷却して
Co基合金粉末を製造した。
そして、各粉末の成分を調べたところ、第１表
のNo.１，２に示す結果であつた。
また、比較のために、Co基合金溶湯をN2ガス
を使用したガス噴霧法により粉化し、酸素を添加
しないN2ガス雰囲気中でそのまま冷却してCo基
合金粉末を製造し、酸素付加処理を行わなかつた
粉末を用意した。この粉末の成分を第１表のNo.３
に示す。
さらに、比較のために、Co基合金溶湯をN2ガ
スを使用したガス噴霧法により粉化したのち水中
で冷却してCo基合金粉末を製造した粉末を用意
した。この粉末の成分を第１表のNo.４に示す。
[Object of the Invention] (Industrial Application Field) The present invention relates to a Co-based alloy powder for powder overlay used in powder overlay welding. (Prior Art) In order to impart corrosion resistance, heat resistance, abrasion resistance, etc. to the surface of a substrate, or to further improve the above characteristics of the substrate surface, surfacing is often performed. Various types of overlay welding methods have been developed, but the powder overlay welding method, which uses powder as a filler material and a plasma arc as a heat source, is particularly popular with the oxyacetylene welding method using a filler rod, TIG It has attracted particular attention in recent years because it is faster and easier to automate than welding methods. The alloy powder used in this powder overlay welding is prepared by spraying gas on the molten alloy and then cooling it in gas, or spraying gas on the molten alloy and then cooling it in liquid (water). The molten alloy is manufactured by a method of spraying liquid (water) onto the molten alloy, a method of applying centrifugal force to the molten alloy, a method of causing the molten alloy to flow down into the gap between rolls rotating at high speed, and the like. In such a powder manufacturing method, when the cooling rate after the molten alloy is powdered by atomizing is slow, the molten alloy becomes spherical due to the surface tension of the molten alloy, but when the cooling rate is high, the molten alloy becomes spherical. The powder solidifies before becoming spheroidized, resulting in an irregularly shaped powder. (Problems to be Solved by the Invention) By the way, the irregularly shaped powder described above has a large length ratio and is not constant, so when this powder is used as a powder for powder overlay, In this case, the feedability of the powder is poor.
Therefore, in the past, various improvements have been made to the powder feeding mechanism, but even so, there are problems such as poor bead shape due to uneven powder feeding, such as lack of hot water, uneven bead width of overlay metal, etc. There was a problem that defects were likely to occur. On the other hand, powder produced by a gas atomization method with a low cooling rate has a spherical shape with a small length ratio, so the powder feedability is good and the bead shape is also good. However, although the bead shape is good, there is a problem that blowholes may occur in the overlay metal. The present invention has been made by focusing on the above-mentioned conventional problems, and has excellent powder feedability.
For powder overlay welding that does not cause problems such as running out of hot water or uneven bead width, has a good bead shape, and does not create blowholes in the overlay metal. The purpose is to provide Co-based alloy powder. [Structure of the Invention] (Means for Solving the Problems) The alloy powder for powder overlay according to the present invention can be used for powder overlay welding in order to improve the wear resistance, heat resistance, corrosion resistance, chemical resistance, etc. of the substrate surface. Co-based alloy powder used for
Si: 5.0% or less, Mn: 3.0% or less, P: 0.03% or less, S: 0.03% or less, Cu: 3.0% or less, Ni: 30%
Below, Cr: 10-40%, W: 20% or less, Mo: 20%
Below, B: 3.0% or less, Fe: 5% or less, N: 0.30
% or less, O: 0.01 to 0.50%, preferably O:
0.02-0.30% and possibly additional Nb:
3.0% or less, Ta: 3.0% or less, V: 3.0% or less,
It is characterized by containing one or more of Zr: 3.0% or less, with the remainder consisting of Co and impurities. Further, in the embodiment of the alloy powder for powder overlay according to the present invention, it is desirable that the length ratio of the alloy powder is 1.5 or less, and the alloy powder is preferably prepared by adjusting the amount of oxygen in the atomizing gas. Te, O:
It can be set at 0.01 to 0.50%. As mentioned above, the alloy powder for powder overlay according to the present invention has an oxygen content of 0.01% by weight or more, and the reason for this is to eliminate as much as possible blowholes in the overlay metal after powder overlay welding. It is. From the viewpoint of eliminating blowholes in the overlay metal, it is sufficient that the amount of oxygen in the powder is 0.50% by weight or less, and more preferably in the range of 0.02 to 0.30% by weight. Further, by setting the nitrogen amount to 0.30% by weight or less, it is possible to reduce or eliminate the occurrence of blowholes in the overlay metal. Furthermore, C is effective in forming carbides and increasing hardness and high-temperature strength, so it should be contained at 0.05% or more, but if it is too large, toughness and ductility will decrease.
It is best to add 3.0% or less, Si reduces non-metallic inclusions in the overlay metal, so it is better to add within 5.0%, and Mn increases the cleanliness of the overlay metal, so 3.0% or less is added. % or less, since P and S impair the toughness of the overlay metal.
It is best to limit both to 0.03% or less. Also,
Cu improves strength, so it may be added up to 3.0%, and Ni contributes to improving corrosion resistance, so it can be added up to 3.0%.
You may add up to Furthermore, since Cr improves corrosion resistance and wear resistance, it is good to add 10% or more, but too much Cr reduces toughness, so it is better to add 40% or less. Furthermore, W can be added up to 20% because it improves wear resistance, and Mo increases corrosion resistance and strength so it can be added up to 20%.
B can be added up to 3.0% because it improves the strength, and Fe can be added up to 5% because it can reduce the cost of the powder without damaging the properties of the overlay metal. In order to improve strength, Nb may be added up to 3.0%, Ta up to 3.0%, V up to 3.0%, Zr
may be added up to 3.0% or less. The alloy powder for powder overlay according to the present invention is made of a Co-based alloy having the above-mentioned composition range, and more preferably has a spherical shape with an length ratio of 1.5 or less. Such a spherical powder is produced by a manufacturing method that involves a cooling rate in which powdered molten metal becomes spherical due to its surface tension and then solidifies, usually a gas atomization method. The alloy powder for powder overlay according to the present invention contains or adheres oxygen in the range of 0.01 to 0.50% in the Co-based alloy powder, and controls the amount of N to 0.30% or less, so that it can be used for overlay metal. However, in order to achieve such an amount of oxygen, for example, there is a method of adjusting the amount of oxygen in the molten metal when melting a Co-based alloy, and a method of adjusting the amount of oxygen in the molten metal in the spray gas. methods of adjusting the amount of oxygen in the atomizing atmosphere (adding oxygen to the atomizing gas if necessary), methods of adjusting the amount of oxygen in the atomizing atmosphere, methods of heat treating the powder to oxidize its surface, methods of pickling the powder and There are methods of oxidizing the surface, etc., and these methods can be used alone or in combination. In addition, a high-oxygen powder and a low-oxygen powder can be mixed so that the powder has an average oxygen content of 0.01 to 0.50%. (Example 1) After melting a Co-based alloy, the molten Co-based alloy was pulverized by a gas atomization method using N 2 gas,
Cool in a gas atmosphere in a chamber adjusted so that the amount of oxygen in N2 gas is 300 to 1000 ppm.
A Co-based alloy powder was produced. When the components of each powder were examined, the results were shown in Nos. 1 and 2 of Table 1. For comparison, Co-based alloy powder was produced by pulverizing Co-based alloy molten metal by a gas atomization method using N 2 gas, and then cooling it as it was in an N 2 gas atmosphere without adding oxygen, followed by oxygen addition treatment. A powder was prepared that had not been subjected to the above steps. The components of this powder are No. 3 in Table 1.
Shown below. Furthermore, for comparison, a Co-based alloy powder was prepared by pulverizing a molten Co-based alloy by a gas atomization method using N 2 gas and then cooling it in water. The components of this powder are shown in No. 4 of Table 1.
【表】
次に、第１表のNo.１〜４に示した組成の各粉末
の球状度（長短比）、流動度（JIS法）を調べたと
ころ、同じく第１表に示す結果であり、ガス噴霧
したのち水中冷却したNo.４の粉末は不規則形状で
あるため長短比が大きく、流動度があまり良くな
い。
続いて、第１表に示した粉末を使用して、第２
表に示す条件で基体表面に粉末肉盛溶接を行つ
た。なお、使用した粉末の粒径は−60〜＋
350meshのものである。[Table] Next, we investigated the sphericity (length ratio) and fluidity (JIS method) of each powder with the composition shown in Nos. 1 to 4 in Table 1, and the results were also shown in Table 1. Powder No. 4, which was cooled in water after being atomized with gas, had an irregular shape, had a large length ratio, and had poor fluidity. Next, using the powder shown in Table 1, a second
Powder overlay welding was performed on the substrate surface under the conditions shown in the table. The particle size of the powder used was -60 to +
It is made of 350mesh.
【表】
次いで、肉盛溶接金属中におけるバルブ100本
中のブローホールの平均個数をＸ線により調べた
ところ、第１表に示す結果であつた。
さらに、肉盛溶接金属の外観不良率をバルブ
100本について調べたところ、同じく第１表に示
す結果であつた。
第１表に示すように、本発明による粉末肉盛用
合金粉末を用いたNo.１，２の場合には、適量の酸
素を有しているため肉盛溶接金属中のブローホー
ル発生がほとんどなく、また、粉末の流動度が高
いため湯切れやビード幅の不均一といつた不具合
がなく、外観不良のない良好な溶接ビード形状を
得ることができた。
これに対して、酸素量が少ないNo.３の粉末を用
いて肉盛溶接を行つた場合には、肉盛溶接金属中
のブローホールが多く、また、長短比の大きい不
規則形状であるNo.４の粉末を用いて肉盛溶接を行
つた場合には、溶接ビード形状が良くなく外観不
良率が高いという好ましくない結果となつた。
（実施例 ２）
Co基合金を溶製したのち、このCo基合金溶湯
をN2ガスを使用したガス噴霧法により粉化し、
そのままガス雰囲気中で冷却してCo基合金粉末
を製造した。
次いで、前記粉末を大気雰囲気中で600℃×１
時間（No.５の場合）および５時間（No.６の場合）
の加熱を行つて酸化させた。そして、各粉末の成
分を調べたところ、第３表のNo.５，６に示す結果
であつた。
また、比較のために、Co基合金溶湯をN2ガス
を使用したガス噴霧法により粉化し、酸素を添加
しないN2ガス雰囲気中でそのまま冷却してCo基
合金粉末を製造し、酸素処理を行わなかつた粉末
を用意した。この粉末の成分を第３表のNo.７に示
す。[Table] Next, the average number of blowholes in 100 valves in the overlay weld metal was examined by X-ray, and the results are shown in Table 1. Furthermore, the appearance defect rate of overlay weld metal can be reduced by valves.
When 100 pieces were investigated, the results were also shown in Table 1. As shown in Table 1, in the case of Nos. 1 and 2 using the alloy powder for powder overlay according to the present invention, there is almost no blowhole generation in the overlay weld metal because it contains an appropriate amount of oxygen. In addition, due to the high fluidity of the powder, there were no problems such as running out of hot water or uneven bead width, and a good weld bead shape with no appearance defects could be obtained. On the other hand, when overlay welding is performed using No. 3 powder with a low oxygen content, there are many blowholes in the overlay weld metal, and No. 3 powder has an irregular shape with a large length ratio. When overlay welding was performed using powder No. 4, the weld bead shape was not good and the appearance defect rate was high, which was an undesirable result. (Example 2) After melting a Co-based alloy, the molten Co-based alloy was pulverized by a gas atomization method using N 2 gas,
Co-based alloy powder was produced by cooling in a gas atmosphere. Next, the powder was heated at 600°C x 1 in an air atmosphere.
time (for No. 5) and 5 hours (for No. 6)
was heated to oxidize it. When the components of each powder were examined, the results were shown in Nos. 5 and 6 of Table 3. For comparison, Co-based alloy powder was produced by pulverizing Co-based alloy molten metal by a gas atomization method using N 2 gas and cooling it as it was in an N 2 gas atmosphere without adding oxygen. A powder that was not processed was prepared. The components of this powder are shown in No. 7 of Table 3.
【表】
次に、第３表のNo.５〜７に示した組成の各粉末
の球状度（長短比）、流動度（JIS法）を調べたと
ころ、同じく第３表に示す結果であつた。
続いて、第３表に示した粉末を使用して、第４
表に示す条件で基体表面に粉末肉盛溶接を行つ
た。なお、使用した粉末の粒径は−60〜＋
350meshのものである。[Table] Next, we investigated the sphericity (long/short ratio) and fluidity (JIS method) of each powder with the composition shown in Nos. 5 to 7 of Table 3, and the results were also shown in Table 3. Ta. Next, using the powder shown in Table 3, the fourth
Powder overlay welding was performed on the substrate surface under the conditions shown in the table. The particle size of the powder used was -60 to +
It is made of 350mesh.
【表】
次いで、肉盛溶接金属中におけるバルブ100本
中のブローホールの平均個数をＸ線により調べた
ところ、第３表に示す結果であつた。
さらに、肉盛溶接金属の外観不良率をバルブ
100本について調べたところ、同じく第３表に示
す結果であつた。
第３表に示すように、本発明による粉末肉盛用
合金粉末を用いたNo.５，６の場合には、適量の酸
素を有しているため肉盛溶接金属中のブローホー
ル発生がほとんどなく、また、粉末の流動度が高
いため湯切れやビード幅の不均一といつた不具合
がなく、外観不良のない良好な溶接ビード形状を
得ることができた。
これに対して、酸素量が少ないNo.７の粉末を用
いて肉盛溶接を行つた場合には、肉盛溶接金属中
のブローホールが多いという好ましくない結果と
なつた。
［発明の効果］
以上説明してきたように、本発明による粉末肉
盛用Co基合金粉末は、重量％で、Ｃ：0.05〜3.0
％、Si：5.0％以下、Mn：3.0％以下、Ｐ：0.03％
以下、Ｓ：0.03％以下、Cu：3.0％以下、Ni：30
％以下、Cr：10〜40％、Ｗ：20％以下、Mo：20
％以下、Ｂ：3.0％以下、Fe：５％以下、Ｎ：
0.30％以下、Ｏ：0.01〜0.50％、場合によつては
さらにNb：3.0％以下、Ta：3.0％以下、Ｖ：3.0
％以下、Zr：3.0％以下のうちの１種または２種
以上を含有し、残部Coおよび不純物よりなるも
のであるから、肉盛溶接時における粉末の送給性
に優れているため肉盛溶接後の溶接ビード形状を
著しく良好なものとすることが可能であると同時
に、肉盛溶接金属中にブローホールが生じるのを
防ぐことが可能であり、粉末を用いた肉盛溶接法
がもつ高速および自動溶接の利点を十分に活すこ
とができるようになるという非常に優れた効果が
もたらされる。[Table] Next, the average number of blowholes in 100 valves in the overlay weld metal was examined by X-ray, and the results are shown in Table 3. Furthermore, the appearance defect rate of overlay weld metal can be reduced by valves.
When 100 pieces were investigated, the results were also shown in Table 3. As shown in Table 3, in the case of Nos. 5 and 6 using the alloy powder for powder overlay according to the present invention, there is almost no occurrence of blowholes in the overlay weld metal because it contains an appropriate amount of oxygen. In addition, due to the high fluidity of the powder, there were no problems such as running out of hot water or uneven bead width, and a good weld bead shape with no appearance defects could be obtained. On the other hand, when overlay welding was performed using No. 7 powder with a low oxygen content, the unfavorable result was that there were many blowholes in the overlay weld metal. [Effects of the Invention] As explained above, the Co-based alloy powder for powder overlay according to the present invention has a C content of 0.05 to 3.0 in weight%.
%, Si: 5.0% or less, Mn: 3.0% or less, P: 0.03%
Below, S: 0.03% or less, Cu: 3.0% or less, Ni: 30
% or less, Cr: 10-40%, W: 20% or less, Mo: 20
% or less, B: 3.0% or less, Fe: 5% or less, N:
0.30% or less, O: 0.01 to 0.50%, in some cases additional Nb: 3.0% or less, Ta: 3.0% or less, V: 3.0
% or less, Zr: 3.0% or less, and the remainder consists of Co and impurities, so it has excellent powder feedability during overlay welding, so it is suitable for overlay welding. It is possible to make the subsequent weld bead shape extremely good, and at the same time, it is possible to prevent blowholes from forming in the overlay weld metal, and the high speed of the overlay welding method using powder can be achieved. This brings about the very excellent effect of being able to take full advantage of the advantages of automatic welding.
Claims (1)
Mn：3.0％以下、Ｐ：0.03％以下、Ｓ：0.03％以
下、Cu：3.0％以下、Ni：30％以下、Cr：10〜40
％、Ｗ：20％以下、Mo：20％以下、Ｂ：3.0％以
下、Fe：５％以下、Ｎ：0.30％以下、Ｏ：0.01〜
0.50％、残部Coおよび不純物よりなることを特徴
とする粉末肉盛用Co基合金粉末。 ２ Co基合金粉末において、Ｏ：0.02〜0.30％で
ある特許請求の範囲１項記載の粉末肉盛用Co基
合金粉末。 ３ 合金粉末は、長短比が1.5以下である特許請
求の範囲第１項または第２項記載の粉末肉盛用
Co基合金粉末。 ４ 合金粉末は、噴霧ガス中の酸素量を調整して
酸素を付加させたものである特許請求の範囲第１
項ないし第３項のいずれかに記載の粉末肉盛用
Co基合金粉末。 ５ 重量％で、Ｃ：0.05〜3.0％、Si：5.0％以下、
Mn：3.0％以下、Ｐ：0.03％以下、Ｓ：0.03％以
下、Cu：3.0％以下、Ni：30％以下、Cr：10〜40
％、Ｗ：20％以下、Mo：20％以下、Ｂ：3.0％以
下、Fe：５％以下、Ｎ：0.30％以下、Ｏ：0.01〜
0.50％、さらにNb：3.0％以下、Ta：3.0％以下、
Ｖ：3.0％以下、Zr：3.0％以下のうちの１種また
は２種以上を含有し、残部Coおよび不純物より
なることを特徴とする粉末肉盛用Co基合金粉末。 ６ Co基合金粉末において、Ｏ：0.02〜0.30％で
ある特許請求の範囲５項記載の粉末肉盛用Co基
合金粉末。 ７ 合金粉末は、長短比が1.5以下である特許請
求の範囲第５項または第６項記載の粉末肉盛用
Co基合金粉末。 ８ 合金粉末は、噴霧ガス中の酸素量を調整して
酸素を付加させたものである特許請求の範囲第５
項ないし第７項のいずれかに記載の粉末肉盛用
Co基合金粉末。[Claims] 1% by weight, C: 0.05 to 3.0%, Si: 5.0% or less,
Mn: 3.0% or less, P: 0.03% or less, S: 0.03% or less, Cu: 3.0% or less, Ni: 30% or less, Cr: 10-40
%, W: 20% or less, Mo: 20% or less, B: 3.0% or less, Fe: 5% or less, N: 0.30% or less, O: 0.01~
A Co-based alloy powder for powder overlay, characterized by comprising 0.50%, the balance being Co and impurities. 2. The Co-based alloy powder for powder overlay according to claim 1, wherein the Co-based alloy powder contains O: 0.02 to 0.30%. 3. The alloy powder is for powder overlay according to claim 1 or 2, wherein the length ratio is 1.5 or less.
Co-based alloy powder. 4. The alloy powder is obtained by adding oxygen by adjusting the amount of oxygen in the atomized gas.
For powder overlay according to any one of Items 1 to 3
Co-based alloy powder. 5 Weight%: C: 0.05 to 3.0%, Si: 5.0% or less,
Mn: 3.0% or less, P: 0.03% or less, S: 0.03% or less, Cu: 3.0% or less, Ni: 30% or less, Cr: 10-40
%, W: 20% or less, Mo: 20% or less, B: 3.0% or less, Fe: 5% or less, N: 0.30% or less, O: 0.01~
0.50%, further Nb: 3.0% or less, Ta: 3.0% or less,
A Co-based alloy powder for powder overlay, characterized in that it contains one or more of V: 3.0% or less, Zr: 3.0% or less, and the balance consists of Co and impurities. 6. The Co-based alloy powder for powder overlay according to claim 5, wherein the Co-based alloy powder contains O: 0.02 to 0.30%. 7. The alloy powder is for powder overlay according to claim 5 or 6, wherein the length ratio is 1.5 or less.
Co-based alloy powder. 8. The alloy powder is obtained by adding oxygen by adjusting the amount of oxygen in the atomized gas.
For powder overlay according to any of Items 7 to 7
Co-based alloy powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60171606A JPS6233090A (en) | 1985-08-02 | 1985-08-02 | Alloy powder for building up of powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60171606A JPS6233090A (en) | 1985-08-02 | 1985-08-02 | Alloy powder for building up of powder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6233090A JPS6233090A (en) | 1987-02-13 |
| JPH0532158B2 true JPH0532158B2 (en) | 1993-05-14 |
Family
ID=15926280
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60171606A Granted JPS6233090A (en) | 1985-08-02 | 1985-08-02 | Alloy powder for building up of powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6233090A (en) |
Families Citing this family (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6418599A (en) * | 1987-07-14 | 1989-01-23 | Kubota Ltd | Composite welding material for plasma pulverulent body welding build-up |
| JPH089115B2 (en) * | 1987-07-14 | 1996-01-31 | 株式会社クボタ | Plasma powder overlay welding material for rolled steel guide member in hot rolling line |
| JPH069755B2 (en) * | 1987-09-30 | 1994-02-09 | 特殊電極株式会社 | Welding material for forming a structure in which carbide is crystallized on the entire surface of the weld metal |
| JPH01165779A (en) * | 1987-12-21 | 1989-06-29 | Fukuda Metal Foil & Powder Co Ltd | Hardening material for inside of cylinder |
| JPH0342194A (en) * | 1989-07-10 | 1991-02-22 | Mitsubishi Heavy Ind Ltd | Marine propeller |
| JPH0494193U (en) * | 1991-01-11 | 1992-08-14 | ||
| JP5742447B2 (en) | 2011-05-09 | 2015-07-01 | 大同特殊鋼株式会社 | High hardness overlaying alloy powder |
| JP6620029B2 (en) | 2015-03-31 | 2019-12-11 | 山陽特殊製鋼株式会社 | Metal powder consisting of spherical particles |
| WO2016158687A1 (en) * | 2015-03-31 | 2016-10-06 | 山陽特殊製鋼株式会社 | Metal powder composed of spherical particles |
| JP7108996B2 (en) * | 2017-12-26 | 2022-07-29 | 新日本溶業株式会社 | Co-Based Alloy for Weld Overlay and Powder for Weld Overlay |
| US11130175B2 (en) * | 2018-01-18 | 2021-09-28 | The Boeing Company | Spherical metallic powder blends and methods for manufacturing the same |
| JP7052493B2 (en) * | 2018-03-30 | 2022-04-12 | トヨタ自動車株式会社 | Alloy powder for overlay and combined structure using this |
| JP7213057B2 (en) * | 2018-10-19 | 2023-01-26 | 山陽特殊製鋼株式会社 | Co-based alloy and its powder |
| DE102021106606A1 (en) | 2020-03-26 | 2021-09-30 | Vdm Metals International Gmbh | Cobalt-chromium alloy powder |
| JP7602338B2 (en) * | 2020-09-11 | 2024-12-18 | 山陽特殊製鋼株式会社 | Co-based alloy and its powder |
-
1985
- 1985-08-02 JP JP60171606A patent/JPS6233090A/en active Granted
Non-Patent Citations (4)
| Title |
|---|
| EUROPEAN SYMPOSIUM ON POWDERMETALLGY=1978 * |
| INTERNATIONAL JOURNAL OF POWDER MATALLURGY=1968 * |
| METALS HANDBOOK NINTH EDITION=1984 * |
| SPECIFICATION FOR SOLID SURFACING WELDING RODS ANDELECTRODES=1980 * |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6233090A (en) | 1987-02-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS6233089A (en) | Ni-based alloy powder for powder overlay | |
| JPH0532158B2 (en) | ||
| CN1233203A (en) | Use of a metal powder for forming a surface coating by submerged arc welding | |
| CN111411319A (en) | A method for preparing nitride-enhanced high-entropy alloy coating by plasma cladding | |
| WO1995005492A1 (en) | Steel containing ultrafine oxide inclusions dispersed therein | |
| CN107717258A (en) | CO 2 gas-shielded low-alloy steel flux-cored wire and its production method | |
| CN106041357B (en) | A kind of nickel toughening high-chromium cast iron-type self protection pile-up welding flux core welding wire and preparation method thereof | |
| JPS60177993A (en) | Powder for plasma overlay welding | |
| JP4373785B2 (en) | Metal powder for thermal coating of substrate | |
| JP2703735B2 (en) | Alloy powder for powder plasma arc welding | |
| US20110290772A1 (en) | Method for arc welding with a dual gas flow, with a central flow containing argon and hydrogen, and with a sheath flow including argon and either carbon dioxide or oxygen | |
| JP2528341B2 (en) | Solid wire for gas shield arc welding | |
| JPH089114B2 (en) | Plasma powder overlay welding powder with good weldability | |
| CN106238964B (en) | A kind of titanium is modified high-chromium cast iron-type self protection pile-up welding flux core welding wire and preparation method thereof | |
| JPS6234672A (en) | Powder overlay welding method | |
| JP3463574B2 (en) | Welding steel wire and method of manufacturing the same | |
| JPH06299286A (en) | Steel with controlled oxide particles and method for producing the same | |
| JP3525191B2 (en) | CO2 gas welding steel wire and method for producing the same | |
| JPH04138893A (en) | Wire for gas shield arc welding | |
| JP2792755B2 (en) | Hearth roll manufacturing method | |
| CN106001993B (en) | A kind of self-fluxing alloyed powder doping vario-property self protection pile-up welding flux core welding wire and preparation method thereof | |
| JP2929515B2 (en) | Solid wire for gas shielded arc welding | |
| JPH05337608A (en) | Production of ni base hot rolling steel material | |
| JPH04172193A (en) | Method for alloying al series base material with cladding by welding | |
| JPH0378195B2 (en) |