JPH0645803B2 - Iron-based self-fluxing alloy powder - Google Patents
Iron-based self-fluxing alloy powderInfo
- Publication number
- JPH0645803B2 JPH0645803B2 JP60111155A JP11115585A JPH0645803B2 JP H0645803 B2 JPH0645803 B2 JP H0645803B2 JP 60111155 A JP60111155 A JP 60111155A JP 11115585 A JP11115585 A JP 11115585A JP H0645803 B2 JPH0645803 B2 JP H0645803B2
- Authority
- JP
- Japan
- Prior art keywords
- iron
- alloy powder
- based self
- fluxing alloy
- wear resistance
- 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
Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は熔射その他の方法により肉盛表面層を形成する
ために使用する耐摩耗性のある鉄基自溶性合金粉に関す
るものである。TECHNICAL FIELD The present invention relates to an iron-based self-fluxing alloy powder having wear resistance, which is used for forming a surfacing surface layer by thermal spraying or another method.
（従来の技術） 溶射等の方法により肉盛表面層を形成するために使用す
る自溶性合金粉は一般的にニッケル基またはコバルト基
に自溶性を付与する成分としてホウ素およびシリコンが
添加されたものを基本組成とし、これにクロム、炭素、
タングステンまたはモリブデンなどの合金成分が添加さ
れている。これらのニッケル基およびコバルト基の自溶
性合金粉はホウ素およびシリコンの自溶性作用により合
金の熔射性、溶融性などが良く、このため肉盛作業性が
非常に良好で、また、耐熱性、耐摩耗性にも比較的すぐ
れている。しかし、自溶性合金の肉盛性と耐摩耗性とに
相反する傾向が認められ、耐摩耗性が要求され特に過酷
な摩耗を受ける条件の個所では肉盛性を性能の主体にお
いたニッケル基およびコバルト基の自溶性合金では満足
されないうえに高価である。そこで、一般的な金属であ
る鉄を用いることも特公昭57−6508号公報等によって提
案されているが、この公報によれば鉄は５％以上添加さ
れると自溶性が低下し目的を達成できないとされてい
る。(Prior Art) The self-fluxing alloy powder used for forming the overlay surface layer by a method such as thermal spraying is generally one in which boron and silicon are added as a component that imparts self-fluxing property to a nickel group or a cobalt group. With the basic composition of chromium, carbon,
An alloy component such as tungsten or molybdenum is added. These nickel-based and cobalt-based self-fluxing alloy powders have good meltability, meltability, etc. of the alloy due to the self-fluxing action of boron and silicon, and therefore have very good build-up workability and heat resistance, It also has relatively excellent wear resistance. However, there is a tendency to conflict with the build-up property and wear resistance of the self-fluxing alloy, and wear resistance is required. Cobalt-based self-fluxing alloys are not satisfactory and expensive. Therefore, it has been proposed to use iron, which is a general metal, in Japanese Examined Patent Publication (Kokoku) No. 57-6508. According to this publication, when 5% or more of iron is added, the self-fluxing property decreases and the object is achieved. It is not possible.
（発明が解決しようとする課題） 本発明が解決しようとするところは前記のような問題点
を解決し、安価な鉄をベースに用いておりながら、特に
過酷な摩耗を受ける条件の個所でも耐摩耗性に優れてい
るとともに肉盛性も良く、しかも、安価な鉄基自溶性合
金粉を提供しようとすることにある。(Problems to be Solved by the Invention) The problem to be solved by the present invention is to solve the above-mentioned problems and to use an inexpensive iron as a base, and to withstand even severely worn conditions. It is an object of the present invention to provide an iron-based self-fluxing alloy powder which is excellent in wear resistance, has good build-up property, and is inexpensive.
（問題点を解決するための手段） 前記のような課題を解決した本発明の鉄基自溶性合金粉
は、重量パーセントで、クロム１０〜３０％、モリブデ
ン５〜１５％、バナジュウム１０％以下、ホウ素１〜５
％、炭素１〜５％、シリコン0.１〜５％、マンガン0.１
〜５％、残部鉄よりなることを特徴とするものである。(Means for Solving Problems) The iron-based self-fluxing alloy powder of the present invention, which has solved the above problems, is 10 to 30% by weight of chromium, 5 to 15% of molybdenum, and 10% or less of vanadium. Boron 1-5
%, Carbon 1-5%, silicon 0.1-5%, manganese 0.1
.About.5%, the balance being iron.
（作用） 以下に本発明の各成分の作用とその限定理由を述べる。(Action) The action of each component of the present invention and the reason for limitation thereof will be described below.
クロムは他の炭化物、ホウ化物を生成する成分とともに
炭素またはホウ素と結びついて硬い複合炭化物また複合
ホウ化物を形成し、耐摩耗性を向上させる。クロムの作
用は含有量が１０％以上で著しくなり、３０％を越える
と合金の融点が高くなり、肉盛作業性が悪くなるから、
クロムの含有量は１０〜３０％に限定される。Chromium, together with other carbide and boride-forming components, combines with carbon or boron to form a hard compound carbide or compound boride, which improves wear resistance. When the content of chromium exceeds 10%, the action of chromium becomes remarkable, and when it exceeds 30%, the melting point of the alloy becomes high and the workability of overlaying is deteriorated.
The chromium content is limited to 10-30%.
モリブデンは５％未満の含有量ではほとんど効果が認め
られないが、５％以上になると含有量の増加にしたがい
硬さおよび耐摩耗性が著しく向上する。しかし１５％を
越えると粗大炭化物が生成し始めて脆くなるから、モリ
ブデンの含有量は５〜１５％に限定される。When molybdenum is less than 5%, almost no effect is observed, but when it exceeds 5%, hardness and wear resistance are remarkably improved as the content increases. However, if it exceeds 15%, coarse carbides start to form and become brittle, so the content of molybdenum is limited to 5 to 15%.
バナジュウムは全く添加しなくても自溶性合金として目
的を達成できるが、耐摩耗性をより向上させるため、１
０％以下の範囲で添加することを必須とする。すなわ
ち、１０％以下の範囲でバナジュウムが添加されている
と微細な炭化物を均一に晶出し、耐摩耗性をより向上さ
せる効果がある。しかし、含有量が１０％を越えるとバ
ナジュウム炭化物はその結晶核数が増加せず、形状が粗
大化し始め、添加量に見合った耐摩耗性の向上も認めら
れなくなるから、バナジュウムの含有量は１０％までで
ある。Vanadium can achieve its purpose as a self-fluxing alloy without any addition, but in order to improve wear resistance, 1
It is indispensable to add in the range of 0% or less. That is, when vanadium is added within the range of 10% or less, fine carbides are uniformly crystallized, and there is an effect of further improving wear resistance. However, if the content exceeds 10%, the number of crystal nuclei of vanadium carbide does not increase, the shape begins to coarsen, and improvement in wear resistance commensurate with the amount added is not observed, so the content of vanadium is 10%. Up to%.
ホウ素はヒュージングの時に酸化物を浮上分離させる自
溶性を付与する成分で、１％以上の含有量になると自溶
性が発揮される。またホウ素は硬いホウ化物を形成する
から耐摩耗性を向上させるための効果的な成分でもある
が、含有量が５％を越えるとホウ化物が多くなり過ぎて
脆くなるから、ホウ素の含有量は１〜５％が適当する範
囲である。Boron is a component that imparts self-solubility to float and separate the oxide during fusing, and the self-solubility is exhibited when the content is 1% or more. Boron is also an effective component for improving the wear resistance because it forms a hard boride, but if the content exceeds 5%, the boride becomes too much and becomes brittle, so the content of boron is 1 to 5% is a suitable range.
炭素は融点を下げて肉盛性を改善すると同時に種々の炭
化物生成成分と結びついて炭化物を生成して耐摩耗性を
向上させる。炭素含有量が１％未満では炭化物の生成が
不充分で耐摩耗性が劣るものとなり、５％を越えると炭
化物量が多くなり過ぎ脆くなるから、炭素含有量の適当
する範囲は１〜５％である。Carbon lowers the melting point to improve the build-up property, and at the same time combines with various carbide-forming components to form carbides and improve wear resistance. If the carbon content is less than 1%, the formation of carbides is insufficient and wear resistance is poor, and if it exceeds 5%, the amount of carbides becomes too large and brittle. Therefore, the appropriate range of carbon content is 1-5%. Is.
なお、本発明は前記したように重量パーセントで、クロ
ム１０〜３０％、モリブデン５〜１５％、バナジュウム
１０％以下、ホウ素１〜５％、炭素１〜５％、シリコン
0.１〜５％、マンガン0.１〜５％、残部鉄よりなること
を特徴とするものであるが、前記した必須の成分以外に
もニッケル１５％以下、コバルト１５％以下のいずれか
一方または双方を含有しておくことが好ましい。その理
由はニッケルおよびコバルトは全く添加しなくも自溶性
合金として作用するが、肉盛時の酸化を低減して肉盛作
業性を改善する作用を有するので、ニッケルとコバルト
のいずれか一方または双方を添加すればそれだけ肉盛作
業性が改善されるからである。しかしながら、両成分は
いずれも高価で合金の価格の上昇をきたすから、ニッケ
ルまたはコバルトの含有量は必要に応じて添加するもの
とし、添加する場合にも経済性を考慮してニッケル、コ
バルトとも１５％以下が適当な量である。As described above, the present invention is, by weight percent, 10 to 30% chromium, 5 to 15% molybdenum, 10% vanadium or less, 1 to 5% boron, 1 to 5% carbon, and silicon.
It is characterized by comprising 0.1 to 5%, manganese 0.1 to 5%, and the balance iron. Either one of nickel 15% or less and cobalt 15% or less in addition to the above-mentioned essential components. Alternatively, both are preferably contained. The reason is that nickel and cobalt act as self-fluxing alloys even if they are not added at all, but since they have the effect of reducing oxidation during overlaying and improving overlaying workability, either or both of nickel and cobalt can be added. This is because the workability of surfacing can be improved by adding. However, both components are expensive and increase the cost of the alloy. Therefore, the content of nickel or cobalt should be added as necessary. Even when adding nickel and cobalt, both nickel and cobalt should be added in an amount of 15% in consideration of economy. % Or less is an appropriate amount.
その他、原料に起因してアルミニウム、リン、イオウな
どの不純分を若干含有することがあっても差支えない。In addition, some impurities such as aluminum, phosphorus, and sulfur may be contained due to the raw materials.
（実施例） 実施例１ クロム１5.４％、モリブデン9.７％、バナジュウム4.８
％、ホウ素4.０％、炭素2.２％、シリコン1.１％、マン
ガン2.９％、残部鉄よりなる鉄基自溶性合金粉および比
較例として市販のクロム１７％、ホウ素3.５％、炭素１
％、シリコン４％、鉄４％、残部ニッケルよりなるニッ
ケル基自溶性合金粉を予めスチール・グリッド・ブラス
トにて前処理した４０mm×６０mm×７mmの一般構造用圧
延鋼材JIS G 3101のSS41製平板に酸素−アセチレン粉末
熔射機を用いて熔射し、その後直ちに同じく酸素−アセ
チレン炎にて加熱ヒュージングして厚さ約1.５mm、ロッ
クウェル硬さHRA86.5の鉄基自溶性合金肉盛層と厚さ約
1.５mm（ロックウェル硬さHRA81.4）のニッケル基自溶
性合金肉盛層とを得た。耐摩耗性の基準試料として合金
工具鋼材JIS G 4404の冷間金型用SKD11製（ロックウェ
ル硬さHRA81）で４０mm×６０mm×8.５mmの平板を用
い、各試料のブラスト摩耗試験を投射材として三河５号
珪砂、投射ノズル孔径９mm、投射圧力５kg/cm2、投射
角度１7.５度、投射距離６０mm、投射時間５分の条件で
行った。その結果、ニッケル基自溶性合金による肉盛層
の耐摩耗性がSKD−11の0.９１倍に対して本実施例の鉄
基自溶性合金粉による肉盛層はSKD−11の1.７２倍の耐
摩耗性を示した。(Example) Example 1 Chromium 15.4%, molybdenum 9.7%, vanadium 4.8
%, Boron 4.0%, carbon 2.2%, silicon 1.1%, manganese 2.9%, iron-based self-fluxing alloy powder consisting of balance iron and commercially available chromium 17% as a comparative example, boron 3.5 %, Carbon 1
% Steel, 4% silicon, 4% iron, balance nickel-based self-fluxing alloy powder pretreated by steel grid blasting 40 mm x 60 mm x 7 mm rolled steel for general structure JIS G 3101 SS41 flat plate Was melted using an oxygen-acetylene powder sprayer, and immediately after that, it was also heat-fused with an oxygen-acetylene flame to a thickness of about 1.5 mm and an iron-based self-fluxing alloy meat of Rockwell hardness HRA86.5. Mori layer and thickness about
A nickel-based self-fluxing alloy overlay having a thickness of 1.5 mm (Rockwell hardness HRA81.4) was obtained. As a reference sample of wear resistance, a blast wear test of each sample was performed by using a flat plate of 40 mm x 60 mm x 8.5 mm made of SKD11 (Rockwell hardness HRA81) made of alloy tool steel JIS G 4404 for cold dies. The conditions were as follows: Mikawa No. 5 silica sand, projection nozzle hole diameter 9 mm, projection pressure 5 kg / cm 2 , projection angle 17.5 degrees, projection distance 60 mm, projection time 5 minutes. As a result, the wear resistance of the build-up layer of the nickel-based self-fluxing alloy was 0.91 times that of SKD-11, whereas the build-up layer of the iron-based self-fluxing alloy powder of this example was 1.72 of SKD-11. The wear resistance was doubled.
実施例２ クロム１1.３％、モリブデン１4.２％、バナジュウム8.
９％、ホウ素4.８％、炭素1.２％、シリコン1.１％、マ
ンガン2.１％、残部鉄よりなる鉄基自溶性合金粉を予め
アルミナ・ブラストにて前処理した７０mm×９０mm×７
mmの一般構造用圧延鋼材JIS G 3101のSS41製平板上に載
せ、窒素ガス雰囲気の炉中にて１１２０℃で１分間加熱
ヒュージングして厚さ約1.５mmロックウェル硬さHRA86.
9の鉄基自溶性合金肉盛層を平板上に得た。端部の肉盛
層は薄かったので厚さが約1.５mmである試料の中央部か
ら肉盛した４０mm×６０mm×約8.５mmの平板を切出し、
ブラスト摩耗試験を投射材として三河５号珪砂、投射ノ
ズル孔径９mm、投射圧力５kg/cm2、投射角度１7.５
度、投射距離６０mm、投射時間５分の条件で耐摩耗性試
験を行った結果、本実施例の鉄基自溶性合金粉による肉
盛層はSKD−11の1.８６倍の耐摩耗性を示した。Example 2 Chromium 11.3%, Molybdenum 14.2%, Vanadium 8.
Iron-based self-fluxing alloy powder consisting of 9%, 4.8% boron, 1.2% carbon, 1.1% silicon, 2.1% manganese, and the balance iron was pre-treated with alumina blast to 70 mm x 90 mm. × 7
Placed on a SS41 flat plate of JIS G 3101 rolled steel for general structure, and heat-fused for 1 minute at 1120 ° C. in a furnace in a nitrogen gas atmosphere to a thickness of about 1.5 mm Rockwell hardness HRA86.
Nine iron-based self-fluxing alloy overlays were obtained on a flat plate. Since the buildup layer at the edge was thin, a 40mm x 60mm x 8.5mm flat plate was cut out from the center of the sample with a thickness of about 1.5mm,
Blast wear test using Mikawa No. 5 silica sand as projection material, projection nozzle hole diameter 9 mm, projection pressure 5 kg / cm 2 , projection angle 17.5.
As a result of a wear resistance test conducted under the conditions of a projection distance, a projection distance of 60 mm and a projection time of 5 minutes, the overlay of the iron-based self-fluxing alloy powder of this example has a wear resistance of 1.86 times that of SKD-11. Indicated.
実施例３ クロム１4.６％、モリブデン１0.０％、バナジュウム5.
１％、ホウ素3.２％、炭素2.４％、シリコン0.３％、マ
ンガン0.３％、ニッケル１3.２％、コバルト１2.８％、
残部鉄よりなる鉄基自溶性合金粉および比較例として市
販のクロム１７％、ホウ素3.５％、炭素１％、シリコン
４％、鉄４％、残部ニッケルよりなるニッケル基自溶性
合金粉を予めスチール・グリッド・ブラストにて前処理
した１９mmφ×２００mmの丸棒表面に酸素−アセチレン
粉末熔射機を用いて熔射し、その後直ちに同じく酸素−
アセチレン炎にて加熱ヒュージングして厚さ約0.５mmの
肉盛層とを得た。この肉盛丸棒より約２０mm×３０mm
の円柱を切出し、切断両端面に２２mm×４mmの円盤状
をした２７％クロム白鋳鉄を同心円状に有機接着剤で接
着し、摩耗試験用試料とした。また合金工具鋼鋼材JIS
G 4404の冷間金型用SKD-11製（ロックウェル硬さHRA8
1）で２０mm×３０mmの円柱の両端に同じく２２mm
×４mmの円盤状をした２７％クロム白鋳鉄を同心円状に
接着して基準試料とした。これらの試料をバレル内容積
１９００ｍ、回転半径２００mmの遠心バレル機を用
い、バレル回転数２００ｒ・ｐ・ｍ・焼成メディア（HC
-T20）1.５kg、コンパウンド（GLC）２cc，水７００m
l，試験時間５時間の条件で摩耗試験を行い、その後両
端面に接着した円盤状をした２７％クロム白鋳鉄および
接着材を除去し、円柱のみの摩耗量を調査した結果、ニ
ッケル基自溶性合金粉粉による肉盛層の耐摩耗性はSKD
−11の0.７９倍であるのに対して、本実施例の鉄基自溶
性合金粉による肉盛層はSKD−11の1.２９倍の耐摩耗性
を示した。Example 3 Chromium 14.6%, Molybdenum 10.0%, Vanadium 5.
1%, Boron 3.2%, Carbon 2.4%, Silicon 0.3%, Manganese 0.3%, Nickel 13.2%, Cobalt 12.8%,
An iron-based self-fluxing alloy powder consisting of the balance iron and a commercially available nickel-based self-fluxing alloy powder consisting of 17% chromium, 3.5% boron, 1% carbon, 4% silicon, 4% iron and the balance nickel was previously prepared as a comparative example. Oxygen was sprayed onto the surface of a 19 mmφ x 200 mm round bar pretreated by steel grid blasting using an acetylene powder sprayer, and immediately thereafter oxygen was also used.
It was heated and fused with an acetylene flame to obtain a built-up layer having a thickness of about 0.5 mm. About 20mm x 30mm from this built-up round bar
The cylinder was cut out, and 22% × 4 mm disk-shaped 27% chrome white cast iron was concentrically adhered with an organic adhesive on both end faces to prepare a sample for abrasion test. In addition, alloy tool steel JIS
Made of SKD-11 for cold mold of G 4404 (Rockwell hardness HRA8
22mm on both ends of a 20mm x 30mm cylinder in 1)
Disc-shaped 27% chrome white cast iron of 4 mm was adhered concentrically to form a reference sample. Using a centrifugal barrel machine with a barrel inner volume of 1900 m and a radius of gyration of 200 mm, these samples were rotated at a barrel rotation speed of 200 r / p / m / firing media (HC
-T20) 1.5kg, compound (GLC) 2cc, water 700m
A wear test was conducted under the conditions of a test time of 5 hours, after which the disc-shaped 27% chrome white cast iron and the adhesive that were adhered to both end surfaces were removed, and the wear amount of only the cylinder was investigated. The wear resistance of the overlay layer made of alloy powder is SKD
While it was 0.79 times that of -11, the overlay of the iron-based self-fluxing alloy powder of this example exhibited a wear resistance that was 1.29 times that of SKD-11.
（発明の効果） 前記説明から明らかなように、従来のニッケル基および
コバルト基の溶射用自溶性合金では耐摩耗性のうえで満
足されず、また、これらの自溶性合金の主成分がニッケ
ルまたはコバルトであるため高価であるという欠点を有
しているのに対し、本発明は鉄を多量に用いておりなが
ら、特に過酷な摩耗を受ける条件の個所でも耐摩耗性に
優れているとともに肉盛性も良くしかも安価な溶射等に
使用する鉄基自溶性合金粉を提供できたもので、本発明
は産業の発達に寄与するところ極めて大なるものがあ
る。(Effects of the Invention) As is clear from the above description, conventional nickel-based and cobalt-based self-fluxing alloys for thermal spraying are not satisfactory in terms of wear resistance, and the main component of these self-fluxing alloys is nickel or In contrast to cobalt, which has the disadvantage of being expensive, the present invention uses a large amount of iron, but is excellent in wear resistance and build-up even under conditions subject to severe wear. The iron-based self-fluxing alloy powder used for thermal spraying and the like has good properties and is inexpensive, and the present invention is extremely large in that it contributes to industrial development.
Claims (1)
モリブデン５〜１５％、バナジュウム１０％以下、ホウ
素１〜５％、炭素１〜５％、シリコン0.１〜５％、マン
ガン0.１〜５％、残部鉄よりなることを特徴とする鉄基
自溶性合金粉。1. By weight percent, 10 to 30% chromium,
Iron base characterized by being composed of molybdenum 5 to 15%, vanadium 10% or less, boron 1 to 5%, carbon 1 to 5%, silicon 0.1 to 5%, manganese 0.1 to 5%, and the balance iron. Self-fluxing alloy powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60111155A JPH0645803B2 (en) | 1985-05-23 | 1985-05-23 | Iron-based self-fluxing alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60111155A JPH0645803B2 (en) | 1985-05-23 | 1985-05-23 | Iron-based self-fluxing alloy powder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61270302A JPS61270302A (en) | 1986-11-29 |
| JPH0645803B2 true JPH0645803B2 (en) | 1994-06-15 |
Family
ID=14553861
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60111155A Expired - Lifetime JPH0645803B2 (en) | 1985-05-23 | 1985-05-23 | Iron-based self-fluxing alloy powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0645803B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008018128A1 (en) * | 2006-08-09 | 2008-02-14 | Ing Shoji Co., Ltd. | Iron-based corrosion resistant wear resistant alloy and deposit welding material for obtaining the alloy |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4322473B2 (en) * | 2002-06-13 | 2009-09-02 | 株式会社東芝 | Water supply pump |
| JP4576854B2 (en) * | 2004-03-10 | 2010-11-10 | 大同特殊鋼株式会社 | High temperature wear resistant member and overlay welding material used therefor |
| US7487840B2 (en) * | 2004-11-12 | 2009-02-10 | Wear Sox, L.P. | Wear resistant layer for downhole well equipment |
| JP4943080B2 (en) * | 2006-07-27 | 2012-05-30 | 山陽特殊製鋼株式会社 | Raw material powder for laser overlay valve seat and valve seat using the same |
| JP5399954B2 (en) | 2009-09-07 | 2014-01-29 | 株式会社フジミインコーポレーテッド | Thermal spray powder |
| JP5748820B2 (en) * | 2009-09-07 | 2015-07-15 | 株式会社フジミインコーポレーテッド | Thermal spray powder, thermal spraying method, thermal spray coating manufacturing method, and thermal spray coating |
| JP5640820B2 (en) * | 2011-03-02 | 2014-12-17 | 新日鐵住金株式会社 | Alloys for liquid phase diffusion bonding |
| CN103060655B (en) * | 2012-10-10 | 2015-05-20 | 北京工业大学 | Preparation method of alloy powder and coating layer for preparing iron-base cladding layer |
| CN102909483A (en) * | 2012-10-24 | 2013-02-06 | 中国航空工业集团公司北京航空材料研究院 | Iron-, cobalt-, nickel- and chrome-base solder for brazing of TiAl and nickel-base superalloy |
| CN109652742A (en) * | 2019-01-17 | 2019-04-19 | 宁波华帆金属材料科技有限公司 | A kind of high alloy iron(-)base powder and its matching method |
| CN114393346B (en) * | 2022-03-02 | 2023-08-04 | 佳木斯大学 | Fe (Fe) 2 B-VB combined reinforced high-boron iron-based wear-resistant surfacing alloy layer and preparation method thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4604781A (en) * | 1985-02-19 | 1986-08-12 | Combustion Engineering, Inc. | Highly abrasive resistant material and grinding roll surfaced therewith |
-
1985
- 1985-05-23 JP JP60111155A patent/JPH0645803B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008018128A1 (en) * | 2006-08-09 | 2008-02-14 | Ing Shoji Co., Ltd. | Iron-based corrosion resistant wear resistant alloy and deposit welding material for obtaining the alloy |
| AU2006347111B2 (en) * | 2006-08-09 | 2011-01-20 | Ing Shoji Co., Ltd. | Iron-based corrosion resistant wear resistant alloy and deposit welding material for obtaining the alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61270302A (en) | 1986-11-29 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US4692305A (en) | Corrosion and wear resistant alloy | |
| EP0223202B1 (en) | Iron alloy containing molybdenum, copper and boron | |
| US4725508A (en) | Composite hard chromium compounds for thermal spraying | |
| EP0138228B1 (en) | Abrasion resistant coating and method for producing the same | |
| US4741974A (en) | Composite wire for wear resistant coatings | |
| US2936229A (en) | Spray-weld alloys | |
| CN101961821B (en) | High temperature resistance and corrosion resistance wear-resistant surfacing electrode | |
| JP4782366B2 (en) | Coating material and products coated with this material | |
| JPH0645803B2 (en) | Iron-based self-fluxing alloy powder | |
| MXPA04008463A (en) | Corrosion resistant powder and coating. | |
| US5966585A (en) | Titanium carbide/tungsten boride coatings | |
| JP2001020052A (en) | Transition metal boride coating | |
| US3974555A (en) | Rolls for rolling mills and method for making same | |
| JP5222553B2 (en) | Abrasion resistant alloy powder and coating | |
| EP0223135A1 (en) | Corrosion resistant self-fluxing alloys for thermal spraying | |
| US3819384A (en) | Flame spraying with powder blend of ferromolybdenum alloy and self-fluxing alloys | |
| US4389251A (en) | Powder mixture for thermal spraying | |
| US2875043A (en) | Spray-weld alloys of the boron-silicon-nickel type | |
| US20140272388A1 (en) | Molten metal resistant composite coatings | |
| US3890137A (en) | Welding powder for producing wear-resistant layers by build-up welding | |
| US3496682A (en) | Composition for producing cutting and/or wearing surfaces | |
| CN114393346B (en) | Fe (Fe) 2 B-VB combined reinforced high-boron iron-based wear-resistant surfacing alloy layer and preparation method thereof | |
| US2184518A (en) | Welding rod and hard overlay deposited therefrom | |
| US4588606A (en) | Abrasion resistant coating and method for producing the same | |
| CN108393605A (en) | High-temperature wearable welding rod and its production method |