JPH0457437B2 - - Google Patents
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- Publication number
- JPH0457437B2 JPH0457437B2 JP29347089A JP29347089A JPH0457437B2 JP H0457437 B2 JPH0457437 B2 JP H0457437B2 JP 29347089 A JP29347089 A JP 29347089A JP 29347089 A JP29347089 A JP 29347089A JP H0457437 B2 JPH0457437 B2 JP H0457437B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- layer
- welding
- build
- heat
- 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
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- 239000000843 powder Substances 0.000 claims description 43
- 239000000463 material Substances 0.000 claims description 25
- 238000003466 welding Methods 0.000 claims description 24
- 239000000919 ceramic Substances 0.000 claims description 18
- 229910052751 metal Inorganic materials 0.000 claims description 15
- 239000002184 metal Substances 0.000 claims description 15
- 239000002245 particle Substances 0.000 claims description 14
- 239000002131 composite material Substances 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 7
- 239000011812 mixed powder Substances 0.000 claims description 5
- 238000002156 mixing Methods 0.000 claims description 3
- 239000010410 layer Substances 0.000 description 23
- 239000011651 chromium Substances 0.000 description 10
- 229910000831 Steel Inorganic materials 0.000 description 8
- 230000003647 oxidation Effects 0.000 description 8
- 238000007254 oxidation reaction Methods 0.000 description 8
- 239000010959 steel Substances 0.000 description 8
- 239000011159 matrix material Substances 0.000 description 7
- 239000000853 adhesive Substances 0.000 description 5
- 230000001070 adhesive effect Effects 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 239000011241 protective layer Substances 0.000 description 3
- 229910000599 Cr alloy Inorganic materials 0.000 description 2
- 230000033228 biological regulation Effects 0.000 description 2
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 2
- 229910010271 silicon carbide Inorganic materials 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000012159 carrier gas Substances 0.000 description 1
- 230000002301 combined effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229910003465 moissanite Inorganic materials 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
- Nonmetallic Welding Materials (AREA)
Description
〔産業上の利用分野〕
本発明は、鋼材加熱炉の炉床金物等の高温用部
材の表面に、耐熱・耐圧縮変形・耐摩耗性にすぐ
れた肉盛層を形成するための金属粉末とセラミツ
ク粉末とからなる複合粉末溶接材に関する。
〔従来の技術〕
耐熱・耐圧縮変形・耐摩耗用材料として、例え
ば、25Cr−20Ni−Fe、25Cr−35Ni−Fe、28Cr
−20Ni−20Co−4W−Fe、または30Cr−20Ni−
40Co−2Mo−Fe等の耐熱鋼が賞用されている。
これらの耐熱鋼製部材は、約1100℃付近までの温
度において優れた耐久性を示す。
〔発明が解決しようとする課題〕
しかしながら、上記耐熱鋼は、スラブ加熱炉の
炉床金物（スキツドレール、スキツドボタン等）
のように、1100℃を越え、1200〜1300℃の高温酸
化雰囲気に曝され、かつ重量物であるスラブの荷
重と、スラブによる摩耗とが加わる条件下に使用
される部材としては、必ずしも十分でなく、表面
の損傷・劣化が進み易い。このような部材の損
耗・劣化は、これに当接する被加熱鋼材の表面品
質を損なう原因となり、またそれを防止するには
炉床部材の早期の取替・修復作業を必要とする
等、炉操業の安定・円滑性を阻害する。このた
め、上記の高温用材料として、1200℃を越える高
温環境下で、よりすぐれた耐圧縮強度、耐酸化性
および耐摩耗性等を保証し得る新たな材料の開発
が強く要請されている。
〔課題を解決するための手段および作用〕
本発明は、上記高温用部材の表面保護層とし
て、高温域における改良された耐圧縮強度、耐酸
化性、および耐摩耗性等を有する肉盛層を形成す
るための溶接材を提供するものである。
本発明に係る溶接肉盛用複合粉末溶接材は、金
属粉末と、炭化物系セラミツク粉末との混合粉末
であつて、
金属粉末は、Co：20.0〜60.0％、残部は実質的
にCrからなる成分組成を有し、
混合粉末に占める炭化物系セラミツク粉末の配
合量は30〜70％であり、
混合粉末の粒度は50〜250メツシユであること、
を特徴としている。
なお、金属粉末の成分組成を示す％、およびセ
ラミツク粉末の配合量を示す％は、いずれも重量
％である。
本発明の肉盛用溶接材は粉末体であるので、肉
盛層の形成には、プラズマ溶接法が適用される。
本発明の複合粉末溶接材を用いてプラズマ溶接
により単層または多層盛りを行つて形成される肉
盛層は、所定成分組成の合金マトリツクスと、そ
のマトリツクス中に分散相として混在するセラミ
ツク粒子とからなる複合組織を有する。
その肉盛層は、後記実施例にも示すように、従
来の耐熱鋼に比し、1200℃以上の高温域における
耐圧縮強度や耐酸化性にすぐれており、また硬度
が高く、良好な耐摩耗性を備えている。しかも、
肉盛層と基材表面との界面は、肉盛溶接時に供給
される十分な量の溶接熱によれ強固な融着結合関
係を形成しており、1200℃の高温域においても、
高い接着強度を失うことがない。
本発明に係る複合粉末溶接材の金属粉末の成分
組成限定理由は次のとおりである。
Co：20.0〜60.0％
Coは高温圧縮強度を高める元素であり、Co−
Cr系合金において、20.0％以上を占めることによ
り顕著な効果が奏せられる。含有量の増加に伴つ
てその効果は強められるが、60.0％を越えると、
マトリツクス金属の融点の低下等により却つて高
温強度の低下をみる。よつて、60.0％を上限とす
る。
Cr：残部
Crは耐酸化性を付与する元素であり、Co−Cr
系合金の基本成分として、40.0〜80.0％を占め
る。なお、Cr含有量が多くなると、マトリツク
ス金属のσ脆化とそれに伴う溶接性の悪化、特に
割れ発生傾向が大きくなるが、80.0％を越えない
範囲内であればそのような不都合は実質的に回避
される。
上記金属粉末に配合されるセラミツク粉末は、
金属マトリツクスに分散相粒子として混在し肉盛
層の耐熱性、高温圧縮強度等を高める。セラミツ
ク粒子は、それ自身、硬度（Hv）：約1500以上と
極めて硬質であるので、マトリツクス中に分散す
ることにより、肉盛層に卓抜した摩耗抵抗性をも
たらす。セラミツク粉末を炭化物系（炭化クロム
Cr3C2，炭化珪素SiC，炭化チタンTiC，炭化タン
グステンWC，W2Ｃ等）としたのは、耐熱性や
耐摩耗性等の点で分散相粒子として好ましいから
である。
複合粉末混合物におけるセラミツク粉末の配合
量を30％以上とするのは、セラミツク粒子の上記
分散結果を十分ならしめるためである。但し、そ
の配合量が70％を越えると、溶接性の悪化、肉盛
層の靭性および基材との接着強度の低下等を招く
ので、70％を上限とする。
更に、粉末の粒度を50メツシユ以上とするの
は、粒径がそれより粗大になると、溶接性が悪く
なり、また肉盛層の高温圧縮強度や基材表面に対
する接着強度等の低下傾向を招くからであり、一
方250メツシユを上限とするのは、それより微細
な粒子では、プラズマ肉盛溶接施工時の粉末のキ
ヤリヤー性が悪く、複合粉末溶接材の送給が不安
定となり、健全な肉盛層の形成が困難ないし不可
能となるからである。
本発明の複合粉末溶接材による肉盛層を形成す
る基材の材質に制限はないが、スラブ加熱炉の炉
床金物等のような場合には、従来より使用されて
いる前記の各種耐熱鋼が好ましく用いられる。
〔実施例〕
第１表に示す粉末を溶接材として、粉末プラズ
マアーク溶接（移行アーク溶接）により、耐熱鋼
基材（20Ni−25Cr−Fe，SUS310相当）の表面
に肉盛層を形成した。いずれも、肉盛層数は３層
であり、層厚は10mmである。
表中、No.１〜８は発明例、No.101〜107は比較例
である。各例におけるセラミツク粉末は炭化クロ
ム（Cr3C2）である。比較例No.101〜107のうち、
No.101は高Co系耐熱合金鋼粉末使用（セラミツ粉
末なし）の例、No.102〜No.107はCo−Cr合金粉末
とセラミツク粉末の組合せであるが、No.102とNo.
103はCo−Cr合金粉末の組成が本発明の規定から
はずれている例（No.102：Co量過剰、Cr量不足、
No.103：Co量不足、Cr量過剰）、No.104とNo.105は
セラミツク粉末配合量が本発明の規定からはずれ
ている例（No.104：セラミツク粉末量過剰、No.
105：同不足）、No.106とNo.107は粉末粒径が本発明
の規定からはずれている例（No.106：粒径粗大、
No.107：粒径微小）である。
〔〕溶接条件
(1) 電圧：35V、電流：120A
(2) 作動ガス：Arガス
プラズマガス ……2.5／min
シールドガス ……20.5／min
キヤリアーガス ……25.5／min
〔〕肉盛層の諸特性
各溶接材を用いて形成された肉盛層の圧縮強度
（Kg／mm2，at1250℃）、硬度（Hv，at1000℃）、基
材表面との接着強度（Kg／mm2，室温）、耐酸化性、
溶接性および溶接施工性を第２表を示す。なお、
耐酸化性は、酸化試験（1200℃、大気雰囲気）に
おける保持時間1000時間での酸化スケール生成に
よる重量減少量から求めた肉盛層表面の酸化損耗
層厚（mm／年）で評価し、溶接性は肉盛層を切断
し、切断面を液体浸透探傷試験に対し、割れの有
無（○：割れなし、×：割れ有り）により評価し
た。また、溶接施工性欄の「○」は、粉末溶接材
の安定な給送により円滑に肉盛層の形成が行われ
たこと、「×」はその給送が不安定で所定の肉盛
層を形成し得なかつたことを表している。
[Industrial Field of Application] The present invention uses metal powder and metal powder for forming a build-up layer with excellent heat resistance, compression deformation resistance, and wear resistance on the surface of high-temperature members such as hearth metal fittings for steel heating furnaces. This invention relates to a composite powder welding material consisting of ceramic powder. [Prior art] Heat-resistant, compressive deformation-resistant, and wear-resistant materials include, for example, 25Cr-20Ni-Fe, 25Cr-35Ni-Fe, and 28Cr.
−20Ni−20Co−4W−Fe, or 30Cr−20Ni−
Heat-resistant steels such as 40Co−2Mo−Fe are widely used.
These heat-resistant steel members exhibit excellent durability at temperatures up to around 1100°C. [Problems to be Solved by the Invention] However, the above-mentioned heat-resistant steel is not suitable for use in hearth hardware (skid rails, skid buttons, etc.) of slab heating furnaces.
It is not necessarily sufficient for a member to be used under conditions where the temperature exceeds 1,100℃ and is exposed to a high-temperature oxidizing atmosphere of 1,200 to 1,300℃, and where the load of a heavy slab and the wear caused by the slab are added. surface damage and deterioration. Wear and deterioration of such parts causes damage to the surface quality of the heated steel materials that come into contact with them, and to prevent this, early replacement and repair of the hearth parts is necessary, etc. It impairs the stability and smoothness of operations. Therefore, there is a strong demand for the development of new materials that can guarantee superior compressive strength, oxidation resistance, abrasion resistance, etc. in high-temperature environments exceeding 1200°C as the above-mentioned high-temperature materials. [Means and effects for solving the problem] The present invention provides a built-up layer having improved compressive strength, oxidation resistance, wear resistance, etc. in a high temperature range, as a surface protective layer of the above-mentioned high temperature member. It provides a welding material for forming. The composite powder welding material for weld overlay according to the present invention is a mixed powder of metal powder and carbide-based ceramic powder, and the metal powder has a composition consisting of 20.0 to 60.0% Co and the remainder substantially Cr. The amount of carbide ceramic powder in the mixed powder is 30 to 70%, and the particle size of the mixed powder is 50 to 250 mesh.
It is characterized by Note that % indicating the component composition of the metal powder and % indicating the blending amount of the ceramic powder are both % by weight. Since the welding material for build-up of the present invention is a powder, a plasma welding method is applied to form the build-up layer. The build-up layer formed by single-layer or multi-layer build-up by plasma welding using the composite powder welding material of the present invention is composed of an alloy matrix of a predetermined composition and ceramic particles mixed as a dispersed phase in the matrix. It has a complex structure. As shown in the examples below, the build-up layer has superior compressive strength and oxidation resistance in the high temperature range of 1200°C or higher, as well as high hardness and good resistance, compared to conventional heat-resistant steel. It has abrasive properties. Moreover,
The interface between the overlay layer and the base material surface forms a strong fusion bond due to the sufficient amount of welding heat supplied during overlay welding, even in the high temperature range of 1200℃.
Never loses high adhesive strength. The reason for limiting the composition of the metal powder of the composite powder welding material according to the present invention is as follows. Co: 20.0-60.0% Co is an element that increases high-temperature compressive strength.
In Cr-based alloys, significant effects can be achieved by occupying 20.0% or more. The effect becomes stronger as the content increases, but when it exceeds 60.0%,
On the contrary, high-temperature strength decreases due to a decrease in the melting point of the matrix metal. Therefore, the upper limit is 60.0%. Cr: Balance Cr is an element that provides oxidation resistance, and Co-Cr
It accounts for 40.0 to 80.0% as a basic component of the alloy. Note that as the Cr content increases, the matrix metal becomes σ-embrittled and the weldability deteriorates, especially the tendency for cracking increases, but as long as the Cr content does not exceed 80.0%, such disadvantages are virtually eliminated. Avoided. The ceramic powder mixed with the above metal powder is
Mixed as dispersed phase particles in the metal matrix, increasing the heat resistance, high-temperature compressive strength, etc. of the overlay layer. Ceramic particles are themselves extremely hard, with a hardness (Hv) of approximately 1500 or more, so by dispersing them in the matrix, they provide the build-up layer with outstanding wear resistance. Ceramic powder is converted into carbide-based (chromium carbide)
Cr 3 C 2 , silicon carbide SiC, titanium carbide TiC, tungsten carbide WC, W 2 C, etc.) are preferred as dispersed phase particles in terms of heat resistance, wear resistance, etc. The reason why the amount of ceramic powder blended in the composite powder mixture is 30% or more is to ensure the above-mentioned dispersion of the ceramic particles is sufficient. However, if the blending amount exceeds 70%, it will cause deterioration in weldability, a decrease in the toughness of the overlay layer, and a decrease in adhesive strength with the base material, so the upper limit is set at 70%. Furthermore, setting the particle size of the powder to 50 mesh or more is because if the particle size becomes coarser, weldability will deteriorate, and the high temperature compressive strength of the overlay layer and the adhesive strength to the base material surface will tend to decrease. On the other hand, the reason why the upper limit is set at 250 meshes is because if the particles are finer than that, the carrier properties of the powder during plasma overlay welding will be poor, and the feeding of the composite powder welding material will become unstable, resulting in poor quality of the welding material. This is because it becomes difficult or impossible to form a raised layer. There are no restrictions on the material of the base material forming the overlay layer using the composite powder welding material of the present invention, but in cases such as hearth metal fittings for slab heating furnaces, various heat-resistant steels as described above, which have been conventionally used, may be used. is preferably used. [Example] Using the powder shown in Table 1 as a welding material, a build-up layer was formed on the surface of a heat-resistant steel base material (20Ni-25Cr-Fe, equivalent to SUS310) by powder plasma arc welding (transfer arc welding). In both cases, the number of built-up layers is three, and the layer thickness is 10 mm. In the table, Nos. 1 to 8 are invention examples, and Nos. 101 to 107 are comparative examples. The ceramic powder in each example is chromium carbide (Cr 3 C 2 ). Among comparative examples No. 101 to 107,
No. 101 is an example of using high Co-based heat-resistant alloy steel powder (no ceramic powder), No. 102 to No. 107 are a combination of Co-Cr alloy powder and ceramic powder, but No. 102 and No.
103 is an example in which the composition of the Co-Cr alloy powder deviates from the specifications of the present invention (No. 102: Excessive amount of Co, insufficient amount of Cr,
No. 103: Insufficient amount of Co, excessive amount of Cr), No. 104 and No. 105 are examples where the amount of ceramic powder blended deviates from the regulations of the present invention (No. 104: Excess amount of ceramic powder, No.
105: Same shortage), No. 106 and No. 107 are examples where the powder particle size deviates from the regulations of the present invention (No. 106: Particle size coarse,
No.107: Particle size is minute). [] Welding conditions (1) Voltage: 35V, current: 120A (2) Working gas: Ar gas plasma gas...2.5/min Shield gas...20.5/min Carrier gas...25.5/min [] Various details of the overlay layer Characteristics Compressive strength (Kg/mm 2 , at 1250℃), hardness (Hv, at 1000℃), adhesive strength with the base material surface (Kg/mm 2 , room temperature), oxidation resistance,
Table 2 shows weldability and weldability. In addition,
Oxidation resistance is evaluated by the oxidation loss layer thickness (mm/year) on the surface of the built-up layer, which is determined from the amount of weight loss due to oxide scale formation after 1000 hours of holding time in an oxidation test (1200℃, air atmosphere). The build-up layer was cut and the cut surface was subjected to a liquid penetrant test to evaluate the presence or absence of cracks (○: no cracks, ×: cracks). In addition, "○" in the welding workability column indicates that the build-up layer was formed smoothly due to stable feeding of the powder welding material, and "x" indicates that the feeding was unstable and the specified build-up layer was not formed. This means that it could not be formed.
【表】【table】
【表】【table】
本発明の複合粉末を肉盛溶接材としてプラズマ
粉体溶接により形成される肉盛層は、マトリツク
ス金属とセラミツク粒子との複合効果により、従
来の耐熱・耐圧縮強度・耐摩耗用材をはるかに凌
ぐ高温特性を備えており、かつ基材表面に対する
接着強度にもすぐれ、特にスラブ加熱炉の炉床金
物等のように、1200℃を越える高温酸化雰囲気
中、スラブ等の重量物の負荷と摩耗をうける苛酷
な条件下に使用される部材の保護層として好適で
あり、これらの部材の耐久性を改善、炉操業の安
定・円滑化に大きく貢献する。その用途は、これ
に限られず、例えば圧延用ワークロール、ガイド
シーリング部材等の表面保護層としても有用であ
る。
The build-up layer formed by plasma powder welding using the composite powder of the present invention as a build-up welding material has far superior heat resistance, compressive strength, and wear resistance due to the combined effect of matrix metal and ceramic particles. It has high-temperature properties and excellent adhesive strength to the base material surface, and is particularly effective against the load and wear of heavy objects such as slabs in high-temperature oxidizing atmospheres exceeding 1200℃, such as hearth hardware of slab heating furnaces. It is suitable as a protective layer for members used under harsh conditions, and it improves the durability of these members and greatly contributes to stabilizing and smoothing furnace operations. Its use is not limited to this, but it is also useful as a surface protective layer for rolling work rolls, guide sealing members, etc., for example.
Claims (1)
粉末からなり、 金属粉末は、Co：20.0〜60.0％、残部は実質的
にCrからなる成分組成を有し、 炭化物系セラミツク粉末の配合量は30〜70％で
あり、 混合粉末の粒度は50〜250メツシユであること
を特徴とするプラズマ溶接肉盛用複合粉末溶接
材。[Scope of Claims] 1. Consisting of a mixed powder of metal powder and carbide ceramic powder, the metal powder has a component composition consisting of Co: 20.0 to 60.0%, the balance substantially consisting of Cr, and the carbide ceramic powder A composite powder welding material for plasma welding overlay, characterized in that the blending amount is 30 to 70%, and the particle size of the mixed powder is 50 to 250 mesh.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29347089A JPH02165896A (en) | 1989-11-10 | 1989-11-10 | Composite powder welding material for weld overlay |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29347089A JPH02165896A (en) | 1989-11-10 | 1989-11-10 | Composite powder welding material for weld overlay |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27560685A Division JPH0238076B2 (en) | 1985-12-06 | 1985-12-06 | YOSETSUNIKUMORYOFUKUGOFUNMATSUYOSETSUZAI |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02165896A JPH02165896A (en) | 1990-06-26 |
| JPH0457437B2 true JPH0457437B2 (en) | 1992-09-11 |
Family
ID=17795166
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29347089A Granted JPH02165896A (en) | 1989-11-10 | 1989-11-10 | Composite powder welding material for weld overlay |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02165896A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4412563B2 (en) * | 2008-07-02 | 2010-02-10 | 住友金属工業株式会社 | High temperature material conveying member |
-
1989
- 1989-11-10 JP JP29347089A patent/JPH02165896A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02165896A (en) | 1990-06-26 |
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