JPH0230396A - Build-up welding method - Google Patents
Build-up welding methodInfo
- Publication number
- JPH0230396A JPH0230396A JP63180009A JP18000988A JPH0230396A JP H0230396 A JPH0230396 A JP H0230396A JP 63180009 A JP63180009 A JP 63180009A JP 18000988 A JP18000988 A JP 18000988A JP H0230396 A JPH0230396 A JP H0230396A
- Authority
- JP
- Japan
- Prior art keywords
- borides
- powder
- alloy powder
- cermet
- welding
- 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 34
- 238000000034 method Methods 0.000 title claims description 11
- 239000000843 powder Substances 0.000 claims abstract description 55
- 239000011195 cermet Substances 0.000 claims abstract description 26
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 23
- 239000000956 alloy Substances 0.000 claims abstract description 23
- 239000002184 metal Substances 0.000 claims abstract description 19
- 229910052751 metal Inorganic materials 0.000 claims abstract description 19
- 229910001256 stainless steel alloy Inorganic materials 0.000 claims 2
- 230000001678 irradiating effect Effects 0.000 claims 1
- 239000000919 ceramic Substances 0.000 abstract description 10
- 229910019918 CrB2 Inorganic materials 0.000 abstract description 2
- 239000000155 melt Substances 0.000 abstract description 2
- 238000007711 solidification Methods 0.000 abstract description 2
- 230000008023 solidification Effects 0.000 abstract description 2
- 229910000531 Co alloy Inorganic materials 0.000 abstract 2
- 229910000990 Ni alloy Inorganic materials 0.000 abstract 2
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 abstract 1
- -1 Mo2B Inorganic materials 0.000 abstract 1
- 229910015173 MoB2 Inorganic materials 0.000 abstract 1
- 229910015346 Ni2B Inorganic materials 0.000 abstract 1
- 229910033181 TiB2 Inorganic materials 0.000 abstract 1
- WRLJWIVBUPYRTE-UHFFFAOYSA-N [B].[Ni].[Ni] Chemical compound [B].[Ni].[Ni] WRLJWIVBUPYRTE-UHFFFAOYSA-N 0.000 abstract 1
- 239000000463 material Substances 0.000 description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910001347 Stellite Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 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 5
- 239000010953 base metal Substances 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 239000011148 porous material Substances 0.000 description 3
- 229910017060 Fe Cr Inorganic materials 0.000 description 2
- 229910002544 Fe-Cr Inorganic materials 0.000 description 2
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000007750 plasma spraying Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000009941 weaving Methods 0.000 description 2
- 229910019590 Cr-N Inorganic materials 0.000 description 1
- 229910019588 Cr—N Inorganic materials 0.000 description 1
- 101150045217 Mobp gene Proteins 0.000 description 1
- 239000004372 Polyvinyl alcohol Substances 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 125000003178 carboxy group Chemical group [H]OC(*)=O 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005552 hardfacing Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229920000609 methyl cellulose Polymers 0.000 description 1
- 239000001923 methylcellulose Substances 0.000 description 1
- 235000010981 methylcellulose Nutrition 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229920002451 polyvinyl alcohol Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000007751 thermal spraying 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
- B23K35/32—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550 degrees C
- B23K35/327—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550 degrees C comprising refractory compounds, e.g. carbides
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Laser Beam Processing (AREA)
Abstract
Description
【発明の詳細な説明】
「産業上の利用分野」
この発明は、表面硬化のための肉盛溶接法に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION "Field of Industrial Application" This invention relates to an overlay welding method for surface hardening.
「従来の技術・発明が解決しようとする課題」従来、バ
ルブ・トリムあるいは回転機械などの耐摩耗性を要求さ
れる部品にはステライト合金(1,0wt%C−28w
t%Cr−残Co )に代表される表面硬化用の肉盛
溶接をしている。しかしながら、このステライト合金は
、肉盛する際、被溶接母材を予熱しこの予熱によって徐
冷を行なわせて溶接割れの発生を防止する必要があった
。このため、予熱温度、徐冷時間などの厳重な熱管理を
必要とし、素材費を含めて施工費がかなり高価になる欠
点があった。また、炭素が溶接時の熱で母材の溶接熱影
響部へ拡散し、母材の耐食性を低下させる欠点があった
。``Prior art/problems to be solved by the invention'' Conventionally, parts such as valves, trims, and rotating machinery that require wear resistance have been manufactured using stellite alloy (1.0wt% C-28W).
We perform overlay welding for surface hardening, which is typified by t%Cr-residue Co. However, when this stellite alloy is overlaid, it is necessary to preheat the base material to be welded and slowly cool it by this preheating to prevent the occurrence of weld cracks. For this reason, strict thermal management such as preheating temperature and slow cooling time is required, which has the disadvantage that construction costs including material costs are quite high. In addition, carbon diffuses into the weld heat affected zone of the base metal due to the heat during welding, resulting in a reduction in the corrosion resistance of the base metal.
そこで、予熱をしなくとも溶接割れが発生しない肉盛溶
接法として、サーメッ、トを金属材料の表面に肉盛りす
るプラズマ溶射、粉体プラズマ溶接が開発されている。Therefore, plasma spraying and powder plasma welding, in which cermet is deposited on the surface of a metal material, have been developed as overlay welding methods that do not cause weld cracks without preheating.
しかしながら、プラズマ溶射は、皮膜中に連続気孔が存
在するため、気孔を通過した腐食液により、皮膜、母材
ともに腐食する可能性があること、あるいは皮膜と母材
との接着強度が十分でなく、苛酷な摩耗環境に適用でき
ないなどの理由で、腐食性の苛酷な環境の肉盛技術とし
ては適していない。However, since plasma spraying has continuous pores in the coating, there is a possibility that both the coating and the base material will be corroded by the corrosive liquid that has passed through the pores, or the adhesive strength between the coating and the base material may be insufficient. , it is not suitable as a build-up technology for corrosive and harsh environments because it cannot be applied to harsh wear environments.
一方、粉体プラズマ溶接(プラズマ・トランスフアート
・アーク溶接)(以下、rPTAJと称する。)では、
高温のプラズマ流を通過したサーメット粉のうち、合金
粉は完全に溶融し、またセラミック粉も半溶融あるいは
溶融状態まで加熱されるため、母材と完全に溶着する。On the other hand, in powder plasma welding (plasma transfer arc welding) (hereinafter referred to as rPTAJ),
Among the cermet powders that have passed through the high-temperature plasma flow, the alloy powder is completely melted, and the ceramic powder is also heated to a semi-molten or molten state, so that it is completely welded to the base material.
また、肉盛層中の気孔もなく、かつ肉盛厚さも自由に制
御できるため、溶射の欠点を克服できる技術といえる。Additionally, there are no pores in the build-up layer, and the build-up thickness can be controlled freely, so it can be said that this technology can overcome the drawbacks of thermal spraying.
このようなサーメットPTA技術としては、たとえば特
開昭55−5126号公報に記載の方法が提案されてい
る。これは、Fe、Ni、CrまたはFe、Crを主成
分とする合金鋼粉末に対し、NbC粉末、VC粉末、T
iC粉末のうちの少なくとも1種以上を添加した粉末
混合物を、アーク中に供給して鉄鋼母材表面に溶接金属
を形成するものである。As such a cermet PTA technique, for example, a method described in Japanese Unexamined Patent Application Publication No. 55-5126 has been proposed. This applies to NbC powder, VC powder, T
A powder mixture containing at least one type of iC powder is supplied into an arc to form weld metal on the surface of a steel base material.
しかしながら、これらの炭化物セラミックスを用いたサ
ーメットでは、プラズマ溶接中に炭化物の一部は溶融あ
るいは分解し、炭素が溶融金属中に固溶するが、その他
の炭化物はほぼ添加した形状で未溶融のまま溶着金属中
に残存する。このため、溶着金属全体にわたって十分な
硬さとなるように炭化物を均一に分散させるためにはか
なり多量の炭化物が必要となる。また、炭素が溶接時の
熱で母材の溶接熱影響部へも拡散し、このため、溶接割
れ感受性が高くなり、また母材の耐食性を著しく低下さ
せるという欠点がある。However, in cermets using these carbide ceramics, some of the carbides melt or decompose during plasma welding, and carbon becomes a solid solution in the molten metal, but other carbides remain unmelted in the form of almost added carbides. Remains in weld metal. Therefore, a fairly large amount of carbide is required in order to uniformly disperse the carbide to provide sufficient hardness throughout the deposited metal. In addition, carbon diffuses into the weld heat-affected zone of the base metal due to the heat during welding, which increases the susceptibility to weld cracking and significantly reduces the corrosion resistance of the base metal.
この発明は、上記事情に鑑みなされたもので、その目的
とするところは、少量のセラミックスの添加で十分な硬
さが得られ、また厳しい熱管理を必要とせず、また母材
の耐食性の低下を拓くことのない肉盛溶接法を提供する
ことにある。This invention was made in view of the above circumstances, and its purpose is to obtain sufficient hardness with the addition of a small amount of ceramics, do not require strict heat management, and reduce the corrosion resistance of the base material. The purpose of the present invention is to provide an overlay welding method that does not require further development.
「課題を解決するための手段」
上記目的を達成するために、この発明の肉盛溶接法は、
Fe−Cr、F’e−Cr−Ni、Fe−Cr−Ni−
Moなどで代表されるステンレス合金粉、またはN i
−Cr、N i −Cr −MoなどのNi基会合金
粉またはCo−Cr、Co−Cr−WなどのCO基会合
金粉、Al2B +t、V B t、CrB 、CrB
t、F eB 、CotB 、N iyB 、Mot
B 、MoB t、T iB tなどのホウ化物の1種
あるいは2種以上を5〜60vt%混合したサーメット
粉をプラズマアーク中に供給して金属または合金上に肉
盛溶接することを特徴とするものである。"Means for Solving the Problem" In order to achieve the above object, the overlay welding method of the present invention:
Fe-Cr, F'e-Cr-Ni, Fe-Cr-Ni-
Stainless alloy powder represented by Mo, or Ni
-Cr, Ni-based metal powder such as Ni-Cr-Mo or CO-based metal powder such as Co-Cr, Co-Cr-W, Al2B +t, VBt, CrB, CrB
t, F eB , CotB , N iyB , Mot
The method is characterized in that cermet powder containing 5 to 60 vt% of one or more borides such as B, MoB, TiB, etc. is supplied into a plasma arc and overlay welded onto a metal or alloy. It is something.
また、Fe−Cr、Fe−Cr−Ni、Fe−Cr−N
i−Moなどで代表されるステンレス合金粉、またはN
i −Cr、Ni −Cr−MoなどのNi基会合金粉
またはCo−Cr、Co−Cr−WなどのCo基会合金
粉、A12B It、V B t、CrB 、CrB
t、F eB 、CotB 、N LB 、MotB
、MoB t、T iB tなどのホウ化物の1種ある
いは2種以上を5〜60wt%混合したサーメット粉を
レーザー・ビーム中に供給して金属または合金上に肉盛
溶接するか、または、金属または合金上にカルボキシ・
メチル・セルロース。Also, Fe-Cr, Fe-Cr-Ni, Fe-Cr-N
Stainless alloy powder represented by i-Mo, or N
Ni-based metal powder such as i-Cr, Ni-Cr-Mo or Co-based metal powder such as Co-Cr, Co-Cr-W, A12B It, V B t, CrB, CrB
t, F eB , CotB , N LB , MotB
Cermet powder containing 5 to 60 wt% of one or more borides such as MoBt, TiBt, etc. is supplied into a laser beam and overlay welded onto metal or alloy, or metal or carboxy on the alloy.
Methyl cellulose.
ポリビニルアルコールなどのバインダーで接着した上記
サーメット粉に、レーザー・ビームを照射して肉盛溶接
するものである。The cermet powder bonded with a binder such as polyvinyl alcohol is irradiated with a laser beam to perform overlay welding.
「作用 」
この発明においては、A12B+!、VBt、CrB、
CrB x、 P eB 、 CotB 、 N 12
B 、MotB 、MoB t、 T iB、などのホ
ウ化物が、いずれもその融点が下表に示すように300
0℃以下と炭化物系のセラミックスより低いため、サー
メット粉をプラズマアークあるいはレーザー・ビームな
どの高温にさらした場合、合金粉ばかりでなくホウ化物
も完全に溶融あるいは分解し、その後、溶着凝固する際
に、再度ホウ化物となって析出する。再析出したホウ化
物は、溶着したサーメット中に細かく、かつ均一に分散
する。"Action" In this invention, A12B+! , VBt, CrB,
CrB x, PeB, CotB, N12
Borides such as B, MotB, MoBt, and TiB all have melting points of 300% as shown in the table below.
Since the temperature is below 0°C, which is lower than that of carbide ceramics, when cermet powder is exposed to high temperatures such as plasma arc or laser beam, not only the alloy powder but also the boride will completely melt or decompose, and then when welding and solidifying. Then, it precipitates again as a boride. The reprecipitated boride is finely and uniformly dispersed in the welded cermet.
(以下余白)
また、ホウ化物系のセラミックスでは、溶融、分解して
も炭素のように母材にまで拡散しない。(Left below) In addition, boride-based ceramics do not diffuse into the base material like carbon, even if they are melted or decomposed.
「実施例」 以下、この発明を実施例により具体的に説明する。"Example" Hereinafter, the present invention will be specifically explained with reference to Examples.
第1図は、Fe −18Cr −12Ni−2Mo(5
US316L)に、CrBtを混合したサーメット粉ま
たはMoBeを混合したサーメット粉を用いてPTAに
よる肉盛溶接を予熱、徐冷などの熱管理なしでそれぞれ
行なった場合の溶着材の硬さと上記ホウ化物の含有量と
の関係を示す図である。なお、同図中にはステライト合
金の標準硬さも図示した。Figure 1 shows Fe-18Cr-12Ni-2Mo(5
The hardness of the welding material and the above boride when overlay welding by PTA was performed on US316L) using cermet powder mixed with CrBt or cermet powder mixed with MoBe without heat management such as preheating and slow cooling. It is a figure showing the relationship with content. In addition, the standard hardness of the stellite alloy is also illustrated in the same figure.
この場合、サーメット粉は、5US316Lの粉にCr
Btの粉またはMOB!の粉を3.5〜65wt%加え
、回転式の混合機を用いて混合した。それぞれの粉末の
粒度は50〜330メツシユの球状粉を用いた。溶接条
件は、
電圧=20〜30V、
電流: 100〜140A1
溶接速度: 100〜200 mm/min。In this case, the cermet powder is 5US316L powder with Cr
Bt powder or MOB! 3.5 to 65 wt% of powder was added and mixed using a rotary mixer. A spherical powder having a particle size of 50 to 330 mesh was used for each powder. Welding conditions are: Voltage = 20-30V, Current: 100-140A1, Welding speed: 100-200 mm/min.
プラズマガス流量=2〜612/ll1in1ウィービ
ング幅: lO〜50IIIIIとした。母材は、長さ
400IIIIlx幅100mmX厚さ16mmの5U
S316L製の平板を用いた。Plasma gas flow rate = 2 to 612/11in1 weaving width: 10 to 50III. The base material is 5U with length 400IIIl x width 100mm x thickness 16mm.
A flat plate made of S316L was used.
この図から、CrBtの含有量が3.5wt%のサーメ
ット粉を肉盛しても、その溶着材の硬さは約240Hv
であり、CrB、を含まない溶着金属の約170Hvに
比較して40%高くなるに過ぎない。しかし、5wt%
以上では約3508v以上でありCrBtを含まない溶
着金属の約2倍以上になり、しかもステライト合金の標
準硬さ約350〜500Hvの下限硬さ約350Hv以
上となっ、た。From this figure, even if we overlay cermet powder with a CrBt content of 3.5 wt%, the hardness of the welding material is approximately 240 Hv.
This is only 40% higher than the approximately 170 Hv of weld metal not containing CrB. However, 5wt%
In the above, it is about 3508 V or more, which is about twice that of the weld metal not containing CrBt, and the lower limit hardness of the standard hardness of Stellite alloy, which is about 350 to 500 Hv, is about 350 Hv or more.
以上の結果から、Cr B tを5wt%以上含有すれ
ば実用上十分な硬度が得られることが判明した。From the above results, it was found that a practically sufficient hardness can be obtained by containing 5 wt% or more of CrBt.
また、MoB、の含有量が3,5wt%のサーメット粉
を肉盛しても、その溶着材の硬さは約250Hvであり
、M o B zを含まない溶着金属の約170Hvに
比較して約50%高くなるに過ぎない。Furthermore, even if cermet powder with a MoB content of 3.5 wt% is deposited, the hardness of the weld material is approximately 250 Hv, compared to approximately 170 Hv of the weld metal that does not contain MoBz. It's only about 50% more expensive.
しかし5wt%以上では約350HvJM上でありM。However, when it is 5wt% or more, it is about 350HvJM or higher.
B、を含まない溶着金属の約2倍以上になり、しかもス
テライト合金の標準硬さの下限以上になった。The hardness was more than twice that of the weld metal not containing B, and moreover, it exceeded the lower limit of the standard hardness for stellite alloys.
以上の結果から、上記CrBtと同様にMoB、を5w
t%以上含有すれば実用上十分な硬さが得られることが
判明した。From the above results, it can be seen that MoB is 5w similar to the above CrBt.
It has been found that practically sufficient hardness can be obtained if the content is t% or more.
第2図は、Fe −18Cr −10Ni −2Mo(
5US316L)にCr B tを65wt%混合した
サーメット粉を用いてPTAによる肉盛溶接を第1図の
場合と同様にして行った場合の溶接部の液体浸透探傷試
験結果を示す金属組織写真である。Figure 2 shows Fe-18Cr-10Ni-2Mo(
5US316L) with 65 wt% of CrBt mixed with cermet powder, PTA overlay welding was carried out in the same manner as in Fig. 1. This is a metallographic photograph showing the results of a liquid penetrant test of a welded part. .
この図から明らかなように、CrBfを65wt%含有
したものでは溶接割れが発生した。As is clear from this figure, weld cracking occurred in the material containing 65 wt% CrBf.
第3図は、Fe −1−8Or −10Ni −2Mo
(5US316L)にCrBfを55wt%混合したサ
ーメット粉を用いてPTAによる肉盛溶接を、第1図の
場合と同様の条件により行なった場合の溶接部の金属組
織写真である。Figure 3 shows Fe-1-8Or-10Ni-2Mo
This is a photograph of the metallographic structure of a welded part when overlay welding by PTA was performed using cermet powder (5US316L) mixed with 55 wt% CrBf under the same conditions as in FIG. 1.
この場合には、溶接割れが発生しなかった。In this case, no weld cracking occurred.
以上の結果から、CrB、の含有量が60vt%以下で
あれば予熱、徐冷などの熱管理なしでも溶接割れが発生
しないことが判明した。From the above results, it was found that weld cracking does not occur even without thermal management such as preheating and slow cooling if the CrB content is 60 vt% or less.
第4図は、5US316L製の仕切り弁の摺動面上(弁
体)に、Fe −18Or −10Ni −2M。FIG. 4 shows Fe-18Or-10Ni-2M on the sliding surface (valve body) of a gate valve made of 5US316L.
(SUS316L)にCrBtを50wt%混合したサ
ーメット粉を用いてPTAによる肉盛溶接を、電圧:2
0V。(SUS316L) with PTA overlay welding using cermet powder mixed with 50 wt% CrBt, voltage: 2
0V.
電流: 120〜140A。Current: 120-140A.
溶接速度+ 150 mm/ min、プラズマガス
流量: 2Q/min。Welding speed + 150 mm/min, plasma gas flow rate: 2Q/min.
ウィービング幅:10mm
の溶接条件で行った後、仕上げ加工したものの金属組織
写真である。This is a photograph of the metallographic structure of the welded material which was finished after welding was carried out under conditions of weaving width: 10 mm.
このCr B tを含むサーメットの溶着材は、切削性
および研磨性などの加工性も優れており、表面硬化肉盛
材料として十分実用性があることが判明した。This cermet welding material containing CrBt has excellent workability such as machinability and polishability, and has been found to be sufficiently practical as a hardfacing material.
さらに、N 1t B 、またはPeB、またはCrB
。Furthermore, N 1t B , or PeB, or CrB
.
とMoBpとをI:1(wt%)の割合で混合してなる
ホウ化物混合物を、それぞれ混合したサーメット粉を用
いて、それぞれについて上記各試験を同様に行ったとこ
ろ、いずれについても上記と同様の効果が得られた。and MoBp in a ratio of I:1 (wt%), and using cermet powder mixed with each, the above-mentioned tests were conducted in the same way, and the results were the same as above. The effect was obtained.
「発明の効果」
以上説明したように、この発明の肉盛溶接法にあっては
、A Q B re V B t 、 Cr B 、
Cr B 2 、 F e B 。"Effects of the Invention" As explained above, in the overlay welding method of the present invention, A Q B re V B t , Cr B ,
CrB2, FeB.
CotB 、N itB 、MO2B 、MOB t、
T iB 2などのホウ化物が、いずれもその融点が3
000℃以下と炭化物系のセラミックスより吸いため、
サーメット粉をプラズマアークあるいはレーザー・ビー
ムなどの高温にさらした場合、合金粉ばかりでなくホウ
化物も完全に溶融あるいは分解し、その後、溶着凝固す
る際に、再度ホウ化物となって析出し、この再析出した
ホウ化物は、溶着したサーメット中に細かく、かつ均一
に分散するので、炭化物系のセラミックスを添加した場
合に比べて少量の添加で溶着部全体にわたって十分な硬
さが得られる。CotB, NitB, MO2B, MOBt,
All borides such as T iB 2 have a melting point of 3
000℃ or less, it absorbs better than carbide ceramics,
When cermet powder is exposed to high temperatures such as plasma arc or laser beam, not only the alloy powder but also the boride completely melts or decomposes, and then, during welding and solidification, it precipitates again as a boride, and this The reprecipitated boride is finely and uniformly dispersed in the welded cermet, so that sufficient hardness can be obtained throughout the welded area with a smaller amount of addition than when carbide ceramics are added.
また、ホウ化物系のセラミックスでは、溶融、分解して
も炭素のように母材にまで拡散しないため、母材の耐食
性を低下さけることがない。In addition, boride-based ceramics do not diffuse into the base material like carbon even if melted or decomposed, so the corrosion resistance of the base material is not reduced.
また、上記ホウ化物の含有量が60wt%以下であれば
、予熱、徐冷などの熱管理をしなくとも溶接割れか生じ
ないので作業性が向上する。Further, if the content of the boride is 60 wt % or less, only weld cracks will occur even without heat management such as preheating and slow cooling, so workability will be improved.
また、上記ホウ化物の含有量が5wt%以上あれば実用
上十分な硬さが得られる。Further, if the content of the boride is 5 wt% or more, practically sufficient hardness can be obtained.
また、サーメット用セラミックスとして多用されている
NbCに比べて、ホウ化物は安価であり、かつ上記のよ
うに少量で効果が大きいことから、経済的に有利である
。Moreover, compared to NbC, which is often used as a ceramic for cermets, borides are inexpensive and, as mentioned above, have a large effect with a small amount, so they are economically advantageous.
第1図ないし第4図はこの発明を説明するための図であ
って、第1図はCrBtの含有量またはMoB、の含有
量と硬さとの関係を示す図、第2図および第3図はそれ
ぞれ溶接部の金属組織写真、第4図は肉盛溶接した仕切
り弁の金属組織写真である。1 to 4 are diagrams for explaining the present invention; FIG. 1 is a diagram showing the relationship between CrBt content or MoB content and hardness; FIGS. 2 and 3 are diagrams showing the relationship between hardness and CrBt content or MoB content; are photographs of the metallographic structure of the welded portion, and Fig. 4 is a photograph of the metallographic structure of the overlay welded gate valve.
Claims (2)
基合金粉に、AlB_1_2、VB_2、CrB、Cr
B_2、FeB、Co_2B、Ni_2B、Mo_2B
、MoB_2、TiB_2などのホウ化物の1種あるい
は2種以上を5〜60wt%混合したサーメット粉をプ
ラズマアーク中に供給して金属または合金上に肉盛溶接
することを特徴とする肉盛溶接法。(1) Stainless steel alloy powder or Ni-based alloy powder or Co
In the base alloy powder, AlB_1_2, VB_2, CrB, Cr
B_2, FeB, Co_2B, Ni_2B, Mo_2B
An overlay welding method characterized by supplying cermet powder containing 5 to 60 wt% of one or more borides such as , MoB_2, TiB_2 into a plasma arc and overlay welding it onto a metal or alloy. .
基合金粉に、AlB_1_2、VB_2、CrB、Cr
B_2、FeB、Co_2B、Ni_2B、Mo_2B
、MoB_2、TiB_2などのホウ化物の1種あるい
は2種以上を5〜60wt%混合したサーメット粉をレ
ーザー・ビーム中に供給して金属または合金上に肉盛溶
接するか、または、金属または合金上に接着した上記サ
ーメット粉に、レーザー・ビームを照射して肉盛溶接す
ることを特徴とする肉盛溶接法。(2) Stainless steel alloy powder or Ni-based alloy powder or Co
In the base alloy powder, AlB_1_2, VB_2, CrB, Cr
B_2, FeB, Co_2B, Ni_2B, Mo_2B
, MoB_2, TiB_2, etc., by supplying cermet powder containing 5 to 60 wt% of one or more borides, such as borides, into a laser beam and overlay welding on the metal or alloy, or An overlay welding method characterized in that overlay welding is performed by irradiating the cermet powder adhered to a laser beam with a laser beam.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP63180009A JPH0230396A (en) | 1988-07-19 | 1988-07-19 | Build-up welding method |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP63180009A JPH0230396A (en) | 1988-07-19 | 1988-07-19 | Build-up welding method |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH0230396A true JPH0230396A (en) | 1990-01-31 |
Family
ID=16075859
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP63180009A Pending JPH0230396A (en) | 1988-07-19 | 1988-07-19 | Build-up welding method |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0230396A (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5247283A (en) * | 1991-03-12 | 1993-09-21 | Matsushita Electric Works, Ltd. | Method for testing smoke sensor and a smoke sensor having a function of executing the test |
EP1711342A1 (en) * | 2004-01-29 | 2006-10-18 | The Nanosteel Company | Wear resistant materials |
JP5242837B1 (en) * | 2012-09-04 | 2013-07-24 | 東芝機械株式会社 | T-die and manufacturing method thereof |
JP2015016570A (en) * | 2013-07-09 | 2015-01-29 | 東芝機械株式会社 | T-die and method for producing the same |
JP2017519641A (en) * | 2014-07-03 | 2017-07-20 | オートテック エンジニアリング エー.アイ.イー. | Reinforced structural parts |
EP3461573A1 (en) * | 2017-10-02 | 2019-04-03 | The Boeing Company | Fabrication of modified alloys using low melting temperature boride compounds for additive manufacturing |
-
1988
- 1988-07-19 JP JP63180009A patent/JPH0230396A/en active Pending
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5247283A (en) * | 1991-03-12 | 1993-09-21 | Matsushita Electric Works, Ltd. | Method for testing smoke sensor and a smoke sensor having a function of executing the test |
US8795448B2 (en) | 2004-01-29 | 2014-08-05 | The Nanosteel Company, Inc. | Wear resistant materials |
EP1711342A1 (en) * | 2004-01-29 | 2006-10-18 | The Nanosteel Company | Wear resistant materials |
JP2013011020A (en) * | 2004-01-29 | 2013-01-17 | Nanosteel Co Inc | Wear resistant material |
EP1711342A4 (en) * | 2004-01-29 | 2008-01-23 | Nanosteel Co | Wear resistant materials |
CN104582932A (en) * | 2012-09-04 | 2015-04-29 | 东芝机械株式会社 | T-die and manufacturing method thereof |
WO2014038490A1 (en) * | 2012-09-04 | 2014-03-13 | 東芝機械株式会社 | T-die and manufacturing method thereof |
JP5242837B1 (en) * | 2012-09-04 | 2013-07-24 | 東芝機械株式会社 | T-die and manufacturing method thereof |
TWI610781B (en) * | 2012-09-04 | 2018-01-11 | 東芝機械股份有限公司 | T-die and manufacturing method thereof |
US10493565B2 (en) | 2012-09-04 | 2019-12-03 | Toshiba Kikai Kabushiki Kaisha | T-die and method of manufacturing the same |
DE112013004338B4 (en) | 2012-09-04 | 2021-12-09 | Shibaura Machine Co., Ltd. | T-nozzle and method of making it |
JP2015016570A (en) * | 2013-07-09 | 2015-01-29 | 東芝機械株式会社 | T-die and method for producing the same |
JP2017519641A (en) * | 2014-07-03 | 2017-07-20 | オートテック エンジニアリング エー.アイ.イー. | Reinforced structural parts |
US10792764B2 (en) | 2014-07-03 | 2020-10-06 | Autotech Engineering S.L. | Reinforced structural components |
EP3461573A1 (en) * | 2017-10-02 | 2019-04-03 | The Boeing Company | Fabrication of modified alloys using low melting temperature boride compounds for additive manufacturing |
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