JPH089115B2 - Plasma powder overlay welding material for rolled steel guide member in hot rolling line - Google Patents
Plasma powder overlay welding material for rolled steel guide member in hot rolling lineInfo
- Publication number
- JPH089115B2 JPH089115B2 JP62175324A JP17532487A JPH089115B2 JP H089115 B2 JPH089115 B2 JP H089115B2 JP 62175324 A JP62175324 A JP 62175324A JP 17532487 A JP17532487 A JP 17532487A JP H089115 B2 JPH089115 B2 JP H089115B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- hot rolling
- layer
- welding material
- rolled steel
- 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
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)
- Coating By Spraying Or Casting (AREA)
- Nonmetallic Welding Materials (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、熱間圧延ラインにおけるガイドローラやサ
イドガイド等の圧延鋼材ガイド部材に、表面保護層とし
て、耐熱性，耐摩耗性，焼付き抵抗性等にすぐれた肉盛
層を形成するためのプラズマ粉体肉盛溶接材料に関す
る。The present invention relates to a rolled steel material guide member such as a guide roller or a side guide in a hot rolling line, which has heat resistance, wear resistance, and seizure as a surface protection layer. The present invention relates to a plasma powder overlay welding material for forming a overlay layer having excellent resistance and the like.
熱間圧延ラインにおけるガイドローラ，サイドガイド
等のガイド部材は、赤熱状態の圧延鋼材の接触・摺接擦
過が繰り返される。このガイド部材の表面保護層とし
て、金属マトリックスに分散相としてセラミック粒子を
混在させた複合組織を有する被覆層を形成することは部
材の耐熱性や体摩耗性等を改善するための極めて有効な
方法である。Guide members such as guide rollers and side guides in the hot rolling line are repeatedly contacted and slidably rubbed with the rolled steel material in a red hot state. As a surface protection layer of this guide member, forming a coating layer having a composite structure in which ceramic particles are mixed as a dispersed phase in a metal matrix is an extremely effective method for improving the heat resistance and body abrasion resistance of the member. Is.
この被覆層の形成方法として、溶射法，溶接肉盛法等
があり、その溶射・溶接材として、炭化珪素（SiC）、
炭化タングステン（WC）等の炭化物系セラミック、アル
ミ（Al2O3）、ジルコニア（ZrO）等の酸化物系セラミッ
クを主体とする複合粉末が工業的に供給されている。As a method of forming this coating layer, there are a thermal spraying method, a weld overlay method, and the like. As the thermal spraying / welding material, silicon carbide (SiC),
A composite powder mainly composed of a carbide ceramic such as tungsten carbide (WC) and an oxide ceramic such as aluminum (Al 2 O 3 ) and zirconia (ZrO) is industrially supplied.
溶射法により形成される被覆層（溶射層）は、基材と
の密着強度に乏しく、機械衝撃により剥離し易いため、
実機使用における安定性や耐久性に問題がある。溶接肉
盛法によれば、基材との密着強度を高めることが可能と
なるが、熱間圧延ラインのガイド部材は、強い機械衝撃
を伴つて赤熱鋼材の接触・擦過が繰り返されるので、そ
のガイド機能を安定に維持させるためには、基材に対す
る肉盛層の密着性をより強化し、かつ耐熱性，耐摩耗性
を高め、また機械衝撃に耐え得る靭性、赤熱鋼材の擦過
に対する焼付き抵抗性等を具備することが要求される。The coating layer (sprayed layer) formed by the spraying method has poor adhesion strength to the base material and is easily peeled off by mechanical impact.
There is a problem with stability and durability in actual use. According to the weld overlay method, it is possible to increase the adhesion strength with the base material, but the guide member of the hot rolling line repeats contact and rubbing of the red hot steel material with a strong mechanical impact, so that In order to maintain a stable guide function, the adhesion of the overlay layer to the base material is further strengthened, heat resistance and wear resistance are improved, and toughness that can withstand mechanical shock and seizure against abrasion of red-hot steel material It is required to have resistance and the like.
本発明は、熱間圧延ラインの鋼材ガイド部材表面の保
護層として上記特性を有する複合肉盛層を形成するため
のプラズマ粉体肉盛溶接材を提供する。The present invention provides a plasma powder overlay welding material for forming a composite overlay layer having the above characteristics as a protective layer on the surface of a steel material guide member of a hot rolling line.
本発明の溶接材は、熱間圧延ラインの圧延鋼材ガイド
部材の表面に、金属マトリックスと炭化物系セラミック
ス粒子とからなる複合肉盛層を形成するための、金属粉
末と炭化物系セラミック粉末との均一な混合物であるプ
ラズマ粉体肉盛溶接材において、 炭化物系セラミック粉末の配合割合は、20〜70重量％
であり、金属粉末は、C4〜８％,Si:2％以下,Mn:2％以
下,Ni:2〜10％,Cr:20〜60％,W:4〜15％、残部実質的にC
oからなることを特徴としている。The welding material of the present invention is a uniform surface of a metal powder and a carbide ceramic powder for forming a composite overlay layer composed of a metal matrix and carbide ceramic particles on the surface of a rolled steel guide member of a hot rolling line. In the plasma powder surfacing welding material, which is a special mixture, the compounding ratio of the carbide ceramic powder is 20 to 70% by weight.
The metal powder is C4-8%, Si: 2% or less, Mn: 2% or less, Ni: 2-10%, Cr: 20-60%, W: 4-15%, and the balance substantially C
It is characterized by consisting of o.
本発明の溶接材は、分散相成分として炭化物系セラミ
ックが配合される。炭化物系セラミック粒子は、硬質で
強度が高く、また金属マトリックスとの濡れもよく、分
散強化粒子としてすぐれている。その好ましい例とし
て、クロム炭化物（Cr3C2、Cr7C3等）、タングステン炭
化物（WC）、チタン炭化物（TiC）、ニオブ炭化物（Nb
C）、炭化珪素（SiC）等が挙げられる。The welding material of the present invention contains a carbide-based ceramic as a dispersed phase component. The carbide-based ceramic particles are hard and have high strength, and also have good wettability with the metal matrix, and are excellent as dispersion strengthening particles. Preferred examples thereof include chromium carbide (Cr 3 C 2 , Cr 7 C 3, etc.), tungsten carbide (WC), titanium carbide (TiC), niobium carbide (Nb
C), silicon carbide (SiC) and the like.
炭化物系セラミック粒子の配合割合（マトリックスと
なる金属分との混合物中に占める重量比）を20％以上と
するのは、その分散強化作用による、高温耐摩耗性およ
び高温強度等の改善効果を十分ならしめるためである。
配合割合を高めるに従って、分散強化作用による硬度、
耐摩耗性、耐熱性、高温強度等が向上するが、70％をこ
えると、溶接施工性が悪化し、溶接ビードを積層して所
要層厚の肉盛層を形成する場合におけるビード積層界面
の密着不良が生じ易くなり、また形成される肉盛層の靭
性が低下、機械的・熱的衝撃による亀裂・剥離等を生じ
易くなる。このため、70％を上限とした。炭化物系セラ
ミック粒子の粒度は、約50〜300メッシュであればよ
い。The blending ratio of carbide-based ceramic particles (weight ratio in the mixture with the metal component of the matrix) of 20% or more is sufficient to improve the effects of improving high-temperature wear resistance and high-temperature strength due to its dispersion strengthening effect. This is because you can train them.
As the blending ratio increases, the hardness due to the dispersion strengthening effect,
Wear resistance, heat resistance, high temperature strength, etc. are improved, but if it exceeds 70%, the weldability deteriorates, and the bead lamination interface in the case of laminating welding beads to form a buildup layer of the required layer thickness Adhesion failure is likely to occur, the toughness of the built-up layer to be formed is lowered, and cracks and peeling due to mechanical and thermal shocks are likely to occur. Therefore, the upper limit was 70%. The size of the carbide-based ceramic particles may be about 50-300 mesh.
マトリックスとなる金属分の成分限定理由は次のとお
りである。The reasons for limiting the components of the metal component forming the matrix are as follows.
C:4〜８％ ＣはCrと結合して金属マトリックス中に炭化物を析出
し、肉盛層の硬度・耐摩耗性を高める。炭化クロムの析
出による硬質・耐摩耗性の改善効果を確保するために、
Ｃ量は、Cr量と関連して４〜８％とする。このＣ量範囲
において、マトリックス金属には、Cr7C3型を主体とす
る炭化クロムが析出生成する。Cr7C3型炭化クロムは極
めて硬質で、配合される炭化物系セラミック粒子の分散
強化作用と相まって、肉盛層に高度の硬度・摩耗抵抗性
を帯有させる。C: 4-8% C combines with Cr to precipitate carbides in the metal matrix and enhances the hardness and wear resistance of the overlay. In order to secure the effect of improving the hardness and wear resistance due to the precipitation of chromium carbide,
The C content is 4-8% in relation to the Cr content. In this C amount range, chromium carbide mainly composed of Cr 7 C 3 type is precipitated and formed in the matrix metal. Cr 7 C 3 type chromium carbide is extremely hard and, in combination with the dispersion strengthening action of the carbide-based ceramic particles to be blended, imparts a high degree of hardness and wear resistance to the overlay layer.
Si:2％以下 Siは溶接肉盛時の溶融金属に流動性を付与する他、脱
酸効果を有する。しかし、その量が２％をこえると、マ
トリックスの靭性の不足をきたすので、これを上限とす
る。Si: 2% or less Si not only imparts fluidity to the molten metal during welding overlay, but also has a deoxidizing effect. However, if the amount exceeds 2%, the toughness of the matrix is insufficient, so this is made the upper limit.
Mn:2％以下 MnはSiと同様に溶接金属を脱酸する。また、不純分で
あるＳをMnSとして固定することにより、低融点化合物
であるFeSの生成を防止する。しかし、その量が多くな
ると、肉盛層中に残存するMnS量が増大し、マトリック
スの清浄度の低下とそれに伴う機械的性質の劣化を生じ
るので、２％以下とする。Mn: 2% or less Mn deoxidizes the weld metal like Si. Further, by fixing S which is an impurity as MnS, the generation of FeS which is a low melting point compound is prevented. However, if the amount of MnS increases, the amount of MnS remaining in the build-up layer increases, resulting in deterioration of the cleanliness of the matrix and deterioration of its mechanical properties, so the content is made 2% or less.
Ni:2〜10％ Niは金属マトリックスの靭性を高めると共に、Crとの
相互作用により耐酸化性を強化する。また分散相である
炭化物系セラミック粒子との濡れ性を良くし、複合組織
の緻密性および均質性を高める。含有量が２％に満たな
いと、上記効果が不足し、他方10％をこえると、マトリ
ックスの融点の低下に起因して、高温域での摩耗抵抗性
が低下し、また赤熱鋼材の接触に対する焼付き抵抗性が
弱くなる。よって２〜10％とする。Ni: 2-10% Ni enhances the toughness of the metal matrix and also enhances the oxidation resistance by interacting with Cr. It also improves the wettability with the carbide-based ceramic particles that are the dispersed phase, and enhances the denseness and homogeneity of the composite structure. If the content is less than 2%, the above effect is insufficient. On the other hand, if it exceeds 10%, the wear resistance in the high temperature range is lowered due to the lowering of the melting point of the matrix, and the contact with the red hot steel material is reduced. The seizure resistance is weakened. Therefore, it is set to 2 to 10%.
Cr:20〜60％ Crはマトリックス金属の耐酸化性を高め、またＣと結
合し炭化クロムを析出して肉盛層の硬度・耐摩耗性を高
める。析出炭化クロムの組成は、Cr量,Cr/Cの量比によ
り異なり、十分なCr量が存在し、かつCr/C比が10以上で
あることにより、Cr7C3を主体とする炭化クロムが生成
する。Cr7C3（Hv約1200〜1500）は、Cr3C（Hv約800〜10
00）等に比べて硬度が高く、耐摩耗性の改善効果が大で
ある。この効果を得るためにCr量は20％以上とする。含
有量の増加に伴ってその効果は増すが、60％を越える
と、靱性が低下し、機械衝撃によるクラックを生じ易く
なるので、これを上限とする。Cr: 20-60% Cr enhances the oxidation resistance of the matrix metal, and also combines with C to precipitate chromium carbide and enhance the hardness and wear resistance of the overlay layer. The composition of the precipitated chromium carbide, Cr amount, depends on the amount ratio of Cr / C, there is sufficient amount of Cr, and by Cr / C ratio is 10 or more, chromium carbide mainly composed of Cr 7 C 3 Is generated. Cr 7 C 3 (Hv approx. 1200 to 1500) is equivalent to Cr 3 C (Hv approx.
The hardness is higher than that of (00) and the like, and the effect of improving wear resistance is great. To obtain this effect, the amount of Cr is set to 20% or more. The effect increases with an increase in the content, but if it exceeds 60%, the toughness deteriorates and cracks due to mechanical impact are likely to occur, so this is the upper limit.
W:4〜15％ ＷはＣと結合し炭化物を形成することにより、金属マ
トリックスの強度を高める。この効果を十分なものとす
るためには４％以上の添加が必要であり、添加量の増加
に伴ってその効果は増す。しかし、Ｗは比重の大きい元
素であるため、あまり多く添加すると、溶融金属中での
偏析による不均一性が著しくなるので、15％を上限とす
る。W: 4 to 15% W increases the strength of the metal matrix by combining with C to form a carbide. In order to make this effect sufficient, it is necessary to add 4% or more, and the effect increases as the amount of addition increases. However, since W is an element having a large specific gravity, if added too much, non-uniformity due to segregation in the molten metal becomes remarkable, so 15% is made the upper limit.
Co:残部 Coは、金属マトリックスと炭化物系セラミック粒子の
濡れ性を高め、分散相粒子の分布を均一化すると共に、
マトリックスと分散相粒子との結合性を良好にする。Co: balance Co enhances the wettability of the metal matrix and the carbide-based ceramic particles, and makes the distribution of the dispersed phase particles uniform,
Improves the bondability between the matrix and the dispersed phase particles.
本発明の溶接材は、上記金属粉末と炭化物系セラミッ
ク粉末との混合物のまま使用することもできるが、必要
に応じて、その粉末混合物を、スプレードライヤ等によ
る公知の造粒処理に付して適当な粒径（例えば50〜300
メッシュ）の造粒粉として使用される。造粒粉として使
用することは、比重の異なる金属粉末とセラミック粉末
との均一な混合状態を確保し、溶接施工の安定性を高め
ると共に、形成される肉盛層の複合組織の均質性を高め
るのに有効な方法である。The welding material of the present invention may be used as it is as a mixture of the metal powder and the carbide ceramic powder, but if necessary, the powder mixture may be subjected to a known granulation treatment by a spray dryer or the like. Suitable particle size (eg 50-300
Used as granulated powder of (mesh). The use as a granulated powder ensures a uniform mixed state of metal powder and ceramic powder having different specific gravities, enhances the stability of welding work, and enhances the homogeneity of the composite structure of the build-up layer to be formed. This is an effective method for
本発明の溶接材を用いてプラズマ粉体溶接肉盛法によ
り部材表面に形成される複合肉盛層は、1000℃前後の高
温域においても高い硬度を有し、高耐摩耗性を示す。ま
た強い衝撃の繰り返しに耐える高靭性を有し、焼付きを
生じ難い安定性をも備えている。その肉盛層と部材との
界面は、溶接熱により形成された強固な融着結合関係を
有し、1200〜1300℃の高温域においても高い接着強度を
失うことがない。なお、肉盛層の層厚は、約３〜20mm程
度であればよい。The composite build-up layer formed on the surface of the member by the plasma powder welding build-up method using the welding material of the present invention has high hardness even in a high temperature range of about 1000 ° C and exhibits high wear resistance. In addition, it has high toughness that can withstand repeated strong impacts and has stability that does not easily cause seizure. The interface between the buildup layer and the member has a strong fusion bonding relationship formed by welding heat, and does not lose high adhesive strength even in a high temperature range of 1200 to 1300 ° C. The layer thickness of the build-up layer may be about 3 to 20 mm.
〔Ｉ〕肉盛溶接材の調製 金属粉末（粒度300メッシュ）と炭化物系セラミック
粉末（粒度200メシュ）との混合粉末に適量の水を添加
てスラリーを調製し、スプレードライヤによる造粒処理
に付し、脱ろう，焼成，および解砕処理を施して、造粒
粉（粒度150メッシュア）を得る。[I] Preparation of Overlay Welding Material An appropriate amount of water is added to a mixed powder of metal powder (particle size 300 mesh) and carbide-based ceramic powder (particle size 200 mesh) to prepare a slurry, which is then subjected to granulation treatment by a spray dryer. Then, dewaxing, firing, and crushing treatment are performed to obtain granulated powder (particle size 150 mesh).
〔II〕肉盛溶接の施工 プラズマ粉体肉盛溶接機により、基板（ステンレス圧
延鋼板,C:0.07％、Cr:24.5％、Ni:20％）（□100×25t,
mm）の表面に、ビードを積層（５層盛り）し、層厚15mm
の肉盛層を形成する。[II] Construction of overlay welding Welded substrate (stainless steel rolled steel sheet, C: 0.07%, Cr: 24.5%, Ni: 20%) ( □ 100 × 25 t ,
mm) surface with beads stacked (5 layers), layer thickness 15 mm
To form a built-up layer of.
〔III〕肉盛層の品質 上記肉盛溶接施工後、試験片を調製し、各種試験を行
って第１表に示す結果を得た。表中、試番（No.）１〜
８は発明例、No.101〜108は比較例である。比較例No.10
1〜108のうち、No.101と102は炭化物系セラミック粒子
の配合量が不足している例、No.103と104は、その配合
量が過剰である例、No.105およびNo.106は、マトリック
ス金属の化学組成が本発明の規定から外れている例（N
o.105はCr量不足、No.106はNi量過剰）であり、またNo.
107は、No.1と同じ複合溶接材を使用して溶射法により
肉盛層を形成した例、No.108はステライト合金（30Cr−
10W−2Fe−1C−Co）の肉盛層（セラミック粒子の配合な
し）の例である。[III] Quality of Overlay Layer After the above overlay welding, test pieces were prepared and various tests were conducted to obtain the results shown in Table 1. In the table, trial number (No.) 1
No. 8 is an invention example, and Nos. 101 to 108 are comparative examples. Comparative example No.10
Of Nos. 1 to 108, No. 101 and 102 are examples in which the amount of carbide-based ceramic particles is insufficient, No. 103 and 104 are examples in which the amount is excessive, No. 105 and No. 106 are , An example in which the chemical composition of the matrix metal deviates from the definition of the present invention (N
o.105 is an insufficient amount of Cr, and No. 106 is an excessive amount of Ni).
No. 107 is an example in which the overlay layer is formed by the thermal spraying method using the same composite welding material as No. 1, No. 108 is a stellite alloy (30Cr-
This is an example of a 10W-2Fe-1C-Co) overlay layer (without mixing ceramic particles).
摩耗試験は下記のリング−ディスク法により行い、摩
耗量（mg/m2）を測定すると共に、摩耗面の焼付き発生
の痕跡の有無を目視観察した。The wear test was performed by the following ring-disk method to measure the amount of wear (mg / m 2 ) and visually observe the presence or absence of a trace of seizure on the worn surface.
摩耗試験（リング−ディスク法）： 円盤状試験材をリング（S25C炭素鋼製）に押圧（荷重
20Kg）。Abrasion test (ring-disk method): Press (load) a disc-shaped test material against a ring (made of S25C carbon steel).
20Kg).
試験温度1000℃、回転数200RPM、摩耗距離1130m、時
間60分。Test temperature 1000 ℃, rotation speed 200RPM, wear distance 1130m, time 60 minutes.
表中、「耐摩耗性」欄の数値は、ステライト合金肉盛
層（No.108）の摩耗量（mg/m2）を１とする比率で表し
ている（数値が小さい程、耐摩耗性良好）。In the table, the values in the "Abrasion resistance" column are expressed as a ratio with the wear amount (mg / m 2 ) of the stellite alloy overlay (No. 108) being 1 (the smaller the value, the greater the wear resistance). Good).
「溶接施工性」の欄は、３層以上のビード積層（層厚
10mm以上）が可能であったものを「○」、不可能であっ
たもの（ビード積層界面の接合不良発生）を「×」で表
している。In the column of "Welding workability", bead lamination of three layers or more (layer thickness
Those that were possible (10 mm or more) are indicated by "○", and those that were impossible (occurrence of bonding failure at the bead lamination interface) are indicated by "x".
第１表に示したように、本発明の溶接材を用いて形成
される複合肉盛層（No.1〜８）は、溶射法により形成さ
れる複合肉盛層（No.107）に比し、基材との密着強度が
高く、また高温域での硬さが高く、ステライト合金肉盛
層（No.108）等に比し摩耗抵抗性にすぐれている。ま
た、摩耗試験における摩擦面の焼付き（ガーリングや疵
の発生）はなく、健全な平滑表面を呈している。しか
も、溶接施工性が良好で、多層盛りも容易である。他
方、セラミック粒子配合割合が不足する場合（No.101,1
02）は高温硬度や耐摩耗性が低く、逆にその配合割合が
過剰の場合（No.103,104）は、溶接施工性に劣る。ま
た、No.105（マトリックス金属のCr量不足）では、耐摩
耗性が低く、No.106（マトリックス金属のNi量過剰）で
は、硬さおよび摩耗抵抗性の改善効果が小さく、しかも
その摩耗試験片の摩擦面には、焼付きによるガーリング
痕跡が観察される。 As shown in Table 1, the composite build-up layers (No. 1 to 8) formed by using the welding material of the present invention are higher than the composite build-up layers (No. 107) formed by the thermal spraying method. However, it has high adhesion strength with the base material and high hardness in the high temperature range, and is superior in abrasion resistance to the stellite alloy overlay layer (No. 108) and the like. In addition, there is no seizure of the frictional surface (occurrence of galling or flaws) in the abrasion test, and a sound smooth surface is exhibited. Moreover, the welding workability is good, and the multi-layer deposition is easy. On the other hand, if the ceramic particle blending ratio is insufficient (No. 101,1
02) has low high-temperature hardness and wear resistance, and conversely, when the mixing ratio is excessive (No. 103, 104), the weldability is poor. No. 105 (insufficient amount of Cr in the matrix metal) has low wear resistance, and No. 106 (excessive amount of Ni in the matrix metal) has little effect on improving hardness and wear resistance. On the friction surface of the piece, a Garling trace due to seizure is observed.
本発明の溶接材を用いてプラズマ粉体肉盛溶接により
形成される複合肉盛層は、基材表面との密着強度が高
く、かつ高温域での耐摩耗性にすぐれ、焼付きに対する
抵抗性等も良好である。また良好な溶接施工性を有し、
多層盛りによる厚い層厚の肉盛層を形成することも容易
である。従って、熱間圧延ラインの圧延鋼材ガイド部材
に適用することにより、部材の耐久性を高め、ガイド機
能を安定に維持する等の効果が得られる。The composite build-up layer formed by plasma powder build-up welding using the welding material of the present invention has high adhesion strength to the surface of the base material, and has excellent wear resistance in a high temperature range and resistance to seizure. Etc. are also good. It also has good weldability.
It is also easy to form a built-up layer having a large layer thickness by a multi-layered buildup. Therefore, by applying it to the rolled steel material guide member of the hot rolling line, the effects of enhancing the durability of the member and stably maintaining the guide function can be obtained.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭48−45450（ＪＰ，Ａ) 特開 昭55−5126（ＪＰ，Ａ) 特開 昭61−293696（ＪＰ，Ａ) 特開 昭62−33090（ＪＰ，Ａ) 日本溶接協会誌「溶接技術」（第34巻, 第８号），産報，Ｐ．45−50 ─────────────────────────────────────────────────── ─── Continuation of the front page (56) Reference JP-A 48-45450 (JP, A) JP-A 55-5126 (JP, A) JP-A 61-293696 (JP, A) JP-A 62- 33090 (JP, A) Japan Welding Association Magazine "Welding Technology" (Vol. 34, No. 8), Industry Report, P.P. 45-50
Claims (1)
面に、金属マトリックスと炭化物系セラミックス粒子と
からなる複合肉盛層を形成するための、金属粉末と炭化
物系セラミック粉末との均一な混合物であるプラズマ粉
体肉盛溶接材において、 炭化物系セラミック粉末の配合割合は、20〜70重量％で
あり、金属粉末は、C4〜８％,Si:2％以下,Mn:2％以下,N
i:2〜10％,Cr:20〜60％,W:4〜15％、残部実質的にCoか
らなることを特徴とする熱間圧延ラインの圧延鋼材ガイ
ド部材用プラズマ粉体肉盛溶接材。1. A uniform mixture of metal powder and carbide ceramic powder for forming a composite build-up layer comprising a metal matrix and carbide ceramic particles on the surface of a rolled steel material guide member of a hot rolling line. In the plasma powder overlay welding material which is, the compounding ratio of the carbide ceramic powder is 20 to 70% by weight, and the metal powder is C4 to 8%, Si: 2% or less, Mn: 2% or less, N
i: 2-10%, Cr: 20-60%, W: 4-15%, the balance consisting essentially of Co, plasma powder build-up welding material for rolled steel material guide members in hot rolling lines .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62175324A JPH089115B2 (en) | 1987-07-14 | 1987-07-14 | Plasma powder overlay welding material for rolled steel guide member in hot rolling line |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62175324A JPH089115B2 (en) | 1987-07-14 | 1987-07-14 | Plasma powder overlay welding material for rolled steel guide member in hot rolling line |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6418598A JPS6418598A (en) | 1989-01-23 |
| JPH089115B2 true JPH089115B2 (en) | 1996-01-31 |
Family
ID=15994088
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62175324A Expired - Lifetime JPH089115B2 (en) | 1987-07-14 | 1987-07-14 | Plasma powder overlay welding material for rolled steel guide member in hot rolling line |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH089115B2 (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5154846A (en) * | 1988-12-27 | 1992-10-13 | Allied-Signal Inc. | Fluorinated butylene oxide based refrigerant lubricants |
| JPH03146297A (en) * | 1989-11-02 | 1991-06-21 | Kubota Corp | Composite member for cavitation resistance and earth and sand wear resistance |
| US5108632A (en) * | 1990-05-10 | 1992-04-28 | Allied-Signal Inc. | Lubricants useful with 1,1-dichloro-2,2,2-trifluoroethane |
| US5185089A (en) * | 1990-05-10 | 1993-02-09 | Allied-Signal Inc. | Lubricants useful with 1,1-dichloro-2,2,2-trifluoroethane |
| JPH0433795A (en) * | 1990-05-30 | 1992-02-05 | Fuji Oozx Kk | Composite hard facing by welding material and engine valve and valve seat welded therewith |
| JPH0433796A (en) * | 1990-05-30 | 1992-02-05 | Fuji Oozx Kk | Composite hard facing by welding material, engine valve and valve seat welded therewith |
| US5100569A (en) * | 1990-11-30 | 1992-03-31 | Allied-Signal Inc. | Polyoxyalkylene glycol refrigeration lubricants having pendant, non-terminal perfluoroalkyl groups |
| US5156768A (en) * | 1991-04-05 | 1992-10-20 | Allied-Signal Inc. | Stabilized chlorine-containing refrigeration compositions |
| WO1992017559A1 (en) * | 1991-04-05 | 1992-10-15 | Allied-Signal Inc. | Stabilized dichlorotrifluoroethane refrigeration compositions |
| CN102233496B (en) * | 2010-04-27 | 2013-05-29 | 昆山京群焊材科技有限公司 | Surfacing welding electrode |
| JP5676808B1 (en) * | 2014-06-25 | 2015-02-25 | 電源開発株式会社 | Co-base alloy for welding, filler metal and overlay metal parts |
| CN107008535A (en) * | 2017-05-31 | 2017-08-04 | 南通高欣耐磨科技股份有限公司 | One kind is inexpensive, can repair HP type Ceramic Composite grinding rollers and manufacture method |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6029982B2 (en) * | 1978-07-27 | 1985-07-13 | 株式会社日立製作所 | Pseudo failure generating device |
| JPS5940212A (en) * | 1982-08-31 | 1984-03-05 | Tokyo Keiso Kk | Liquid level measuring device |
| JPS6221063A (en) * | 1985-07-22 | 1987-01-29 | Toshiba Corp | Suction and exhaust apparatus of automatic chemical analysis facility |
| JPS6233090A (en) * | 1985-08-02 | 1987-02-13 | Daido Steel Co Ltd | Alloy powder for building up of powder |
-
1987
- 1987-07-14 JP JP62175324A patent/JPH089115B2/en not_active Expired - Lifetime
Non-Patent Citations (1)
| Title |
|---|
| 日本溶接協会誌「溶接技術」（第３４巻，第８号），産報，Ｐ．４５−５０ |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6418598A (en) | 1989-01-23 |
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