JPH0334278Y2 - - Google Patents
Info
- Publication number
- JPH0334278Y2 JPH0334278Y2 JP7910585U JP7910585U JPH0334278Y2 JP H0334278 Y2 JPH0334278 Y2 JP H0334278Y2 JP 7910585 U JP7910585 U JP 7910585U JP 7910585 U JP7910585 U JP 7910585U JP H0334278 Y2 JPH0334278 Y2 JP H0334278Y2
- Authority
- JP
- Japan
- Prior art keywords
- hammer
- weld metal
- metal
- hardfacing
- coal
- 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
Links
- 229910052751 metal Inorganic materials 0.000 claims description 34
- 239000002184 metal Substances 0.000 claims description 34
- 239000003245 coal Substances 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 7
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 7
- 239000000203 mixture Substances 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 239000000126 substance Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 239000011435 rock Substances 0.000 claims description 3
- 229910052721 tungsten Inorganic materials 0.000 claims description 3
- 238000005552 hardfacing Methods 0.000 description 15
- 239000011651 chromium Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 229910001208 Crucible steel Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000010742 number 1 fuel oil Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Crushing And Pulverization Processes (AREA)
Description
〔産業上の利用分野〕
本考案は石炭・岩石等を破砕するクラツシヤの
ハンマに関する。
〔従来の技術〕
COM（coal oil mixture）やCWM（coal
water mixture）などの燃料を製造する過程にお
いて、原料石炭を破砕し数mm以下の細かい粒子に
する必要があり、ここで破砕機（クラツシヤ）が
使われる。
第２図は従来クラツシヤの構造を示すものであ
る。
０１はハンマであり、ハンマ０１はロータデイ
スク０２に取り付けられる。０３はブレーカプレ
ート、０４はグレート、０５は給炭口である。原
料炭は、給炭口０５から供給され、約1000rpmで
回転しているロータデイスク０２に取り付けられ
たハンマ０１に衝突し、破砕される。またハンマ
０１に衝突し破砕され飛散する石炭はさらにブレ
ーカプレート０３にも衝突し破砕される。破砕さ
れた石炭は、さらにハンマ０１とグレート０４の
間で粉砕され、グレート０４の間隙を通過してク
ラツシヤの外へ送り出される。
第３図は約100H運転した後のハンマの状況を
示す。０１ａはハンマ本体であり、Ni−Cr−Mo
鋳鋼を熱処理によりビツカース硬さで約Hv550と
したものであり、０５は約100H運転後摩耗した
部分である。
〔考案が解決しようとする問題点〕
従来のNi−Cr−Mo鋳鋼を熱処理によつて硬化
したハンマでは短時間の運転でハンマの破砕面の
摩耗が進み石炭の破砕性能が低下し、新製のハン
マと交換する必要があり、その交換に要する時間
及び経済的負担が大であつた。
従つて、長時間の運転に耐える高耐摩性ハンマ
の開発が望まれている。
〔問題点を解決するための手段〕
本考案は石炭や岩石を破砕するクラツシヤのハ
ンマにおいて、上記ハンマ破砕面にオーステナイ
ト系ステンレス鋼の溶接金属を形成した上に化学
成分が、重量パーセントでＣ：5.0〜6.0％、Cr：
20〜30％、Nb：2.0〜8.0％、Mo：0.3〜6.0％、
Ｗ：2.0〜5.0％、Ｖ：0.2〜3.0％、残部を鉄及び
不可避的不純物となる溶接金属を厚さが５mm以
上、20mm以下の範囲で形成させたことを特徴とす
る。
〔作用〕
鋼製ハンマの破砕面に高炭素・高クロム系の硬
化肉盛溶接金属を形成させ、その溶接金属中の高
硬度の晶出炭化物によつて耐摩耗性を向上させ
る。また、ハンマ母材と硬化肉盛溶接金属との間
にオーステナイト系ステンレス鋼の溶接金属を形
成させることによつて硬化肉盛溶接金属の剥離割
れを防止する。
〔実施例〕
第１図に本考案の一実施例を示す。
１はハンマ本体であり、Ni−Cr−Mo鋳鋼を焼
入、焼戻し熱処理を施し、硬さをビツカース硬さ
でHv260に調整したものである。１ａはオーステ
ナイト系ステンレス鋼SUS309の溶接金属であ
り、ハンマの破砕面に被覆アーク溶接法にて２mm
厚さの溶接金属を形成したものである。１ｂはオ
ーステナイト系ステンレス鋼SUS309の溶接金属
１ａの上に形成された約７mm厚さの硬化肉盛溶接
金属であり、その化学成分は重量パーセントで
Ｃ：5.5％、Cr：28.5％、Nb：4.0％、Mo：1.0
％、Ｗ：4.0％、Ｖ：0.7％であり、表面の硬さは
シヨア硬さで約Hs90であつた。なお、硬化肉盛
溶接金属は被覆アーク溶接法によつて形成したも
のである。
本考案であるハンマと従来のハンマを実機のク
ラツシヤに取り付け100Hの石炭破砕試験を行つ
た結果、従来のハンマの最大摩耗深さは15mmであ
つたのに対し、本考案のハンマの最大摩耗深さは
３mmであり、硬化肉盛金属の剥離等の損傷もなく
本考案ハンマの耐摩耗性が従来のハンマと比較し
て非常に優れることが確認された。
第１表は本考案の実験結果を示すものである。
石炭破砕能力3ton／Ｈの試験用クラツシヤのハン
マ１に種々のハンマを取り付け100Hの破砕試験
を行い、その結果を示したものである。
試験番号１〜４は硬化肉盛金属のＣの影響を示
したものであり、Ｃが5.0％未満では摩耗量が大
きく、6.0％を超えると硬化肉盛金属に剥離割れ
が発生する。
試験番号５〜８は同じくCrの影響を示したも
のであり、Cr量が20％以上から耐摩耗性が向上
し、30％を超えるとその効果は低減する。
試験番号９〜12はNbの添加量の影響を示した
ものであり、Nb量が2.0％未満では耐摩耗性が悪
く、８％を超えるとその添加の効果が少なくな
り、高価なNbを８％を超して添加することは実
用的ではない。
試験番号13〜16はMoの添加量の影響を示した
ものであり、Mo量0.3％未満では耐摩耗性が悪
く、６％を超えるとその添加の効果は薄くなる。
試験番号17〜20はＷの添加量の影響を示したも
のであり、Ｗ量が2.0％未満では耐摩耗性が悪く、
５％を超すと硬化肉盛金属に剥離割れが発生す
る。
試験番号21〜24はＶの添加量の影響を示したも
のであり、Ｖ量が0.2％未満では耐摩耗性が不足
し、３％を超えるとＶ添加の効果が薄れるため、
高価なＶの添加量を３％超すことは実用的ではな
い。
以上試験番号１〜24はハンマ破砕面にSUS309
の溶接金属を約２mm形成し、その上に種々の化学
成分の硬化肉盛金属を10mm厚さ形成したものであ
る。なお溶接金属は全て被覆アーク溶接法によつ
て形成した。
試験番号１〜24の結果より、ハンマの耐摩耗性
を向上させるための硬化肉盛金属の成分は、重量
パーセントでＣ：5.0〜6.0％、Cr：20〜30％、
Nb：2.0〜8.0％、Mo：0.3〜6.0％、Ｗ：2.0〜5.0
％、Ｖ：0.2〜3.0％、残部を鉄及び不可避的不純
物よりなる化学成分が適している。
試験番号25〜27はハンマの破砕面に直接硬化肉
盛金属を形成させたものであるが、何れも剥離割
れが発生しており、オーステナイト系ステンレス
鋼SUS309の下盛が必要であることが示される。
試験番号28〜29は硬化肉盛金属の厚さをそれぞ
れ15mm、20mm、23mmと変化させたものであるが、
硬化肉盛金属の厚さが20mmを超えると剥離割れが
発生する。
また硬化肉盛金属の厚さは５mm以上形成させな
いと、母材の影響で硬さが不足するため、硬化肉
盛金属の厚さは５〜20mmが適正である。
〔考案の効果〕
本考案は鋼製ハンマの破砕面に形成させた高炭
素・高クロム系の硬化肉盛溶接金属の高硬度の晶
出炭化物によつて耐摩耗性を向上させる。また、
ハンマ母材と硬化肉盛溶接金属との間に形成させ
たオーステナイト系ステンレス鋼によつて硬化肉
盛溶接金属の剥離割れを防止する。
[Industrial Application Field] The present invention relates to a crusher hammer for crushing coal, rocks, etc. [Conventional technology] COM (coal oil mixture) and CWM (coal oil mixture)
In the process of manufacturing fuels such as water mixture, it is necessary to crush raw coal into fine particles of several millimeters or less, and a crusher is used here. FIG. 2 shows the structure of a conventional crusher. 01 is a hammer, and the hammer 01 is attached to the rotor disk 02. 03 is a breaker plate, 04 is a grate, and 05 is a coal feed port. Raw coal is supplied from a coal feed port 05, collides with a hammer 01 attached to a rotor disk 02 rotating at about 1000 rpm, and is crushed. Further, the coal that collides with the hammer 01, is crushed and scattered, further collides with the breaker plate 03, and is crushed. The crushed coal is further crushed between the hammer 01 and the grate 04, passes through the gap between the grate 04, and is sent out of the crusher. Figure 3 shows the condition of the hammer after approximately 100 hours of operation. 01a is the hammer body, made of Ni-Cr-Mo
The cast steel is heat-treated to a Bitkers hardness of about Hv550, and 05 is the part worn after about 100 hours of operation. [Problems that the invention aims to solve] With conventional hammers made of Ni-Cr-Mo cast steel hardened through heat treatment, the crushing surface of the hammer progresses to wear after a short period of operation, and the coal crushing performance deteriorates. It was necessary to replace the hammer with a new one, and the time and economic burden required for the replacement was large. Therefore, it is desired to develop a hammer with high wear resistance that can withstand long-term operation. [Means for Solving the Problems] The present invention provides a crusher hammer for crushing coal or rock, in which an austenitic stainless steel weld metal is formed on the crushing surface of the hammer, and the chemical composition is C: 5.0~6.0%, Cr:
20~30%, Nb: 2.0~8.0%, Mo: 0.3~6.0%,
It is characterized in that W: 2.0 to 5.0%, V: 0.2 to 3.0%, and the balance is iron and weld metal which becomes unavoidable impurities, with a thickness in the range of 5 mm or more and 20 mm or less. [Operation] Forms a high-carbon, high-chromium hardened overlay weld metal on the crushing surface of the steel hammer, and improves wear resistance due to the highly hard crystallized carbides in the weld metal. Further, by forming an austenitic stainless steel weld metal between the hammer base material and the hardfacing weld metal, peeling cracks in the hardfacing weld metal are prevented. [Embodiment] FIG. 1 shows an embodiment of the present invention. 1 is the hammer body, which is made of Ni-Cr-Mo cast steel and subjected to quenching and tempering heat treatment, and the hardness is adjusted to Hv260 in terms of Vickers hardness. 1a is welded metal of austenitic stainless steel SUS309, and a 2mm welded metal is applied to the fractured surface of the hammer by covered arc welding.
Thick welded metal is formed. 1b is a hardened overlay weld metal with a thickness of about 7 mm formed on weld metal 1a of austenitic stainless steel SUS309, and its chemical composition is C: 5.5%, Cr: 28.5%, Nb: 4.0 in weight percent. %, Mo: 1.0
%, W: 4.0%, V: 0.7%, and the surface hardness was approximately Hs90 in Shore hardness. Note that the hardfacing weld metal was formed by a covered arc welding method. The hammer of the present invention and the conventional hammer were attached to an actual crusher and a 100H coal crushing test was conducted. As a result, the maximum wear depth of the conventional hammer was 15 mm, while the maximum wear depth of the hammer of the present invention was 15 mm. The height was 3 mm, and there was no damage such as peeling of the hardfacing metal, and it was confirmed that the abrasion resistance of the hammer of the present invention was extremely superior compared to conventional hammers. Table 1 shows the experimental results of the present invention.
Various hammers were attached to hammer 1 of a test crusher with a coal crushing capacity of 3 tons/H, and a crushing test was conducted for 100 hours, and the results are shown. Test numbers 1 to 4 show the influence of C on the hardfacing metal; when C is less than 5.0%, the amount of wear is large, and when it exceeds 6.0%, peeling cracks occur in the hardfacing metal. Test numbers 5 to 8 similarly show the influence of Cr; wear resistance improves when the amount of Cr exceeds 20%, and the effect decreases when the amount of Cr exceeds 30%. Test numbers 9 to 12 show the influence of the amount of Nb added; if the amount of Nb is less than 2.0%, the wear resistance is poor, and if it exceeds 8%, the effect of the addition is reduced. It is not practical to add more than %. Test numbers 13 to 16 show the influence of the amount of Mo added; if the Mo amount is less than 0.3%, the wear resistance is poor, and if it exceeds 6%, the effect of the addition becomes weaker. Test numbers 17 to 20 show the influence of the amount of W added; when the amount of W is less than 2.0%, the wear resistance is poor;
If it exceeds 5%, peeling cracks will occur in the hardfacing metal. Test numbers 21 to 24 show the effect of the amount of V added; if the amount of V is less than 0.2%, the wear resistance is insufficient, and if it exceeds 3%, the effect of V addition is weakened.
It is not practical to add more than 3% of expensive V. In the above test numbers 1 to 24, the hammer crushing surface was made of SUS309.
A weld metal of approximately 2 mm is formed, and hardened overlay metals of various chemical compositions are formed on top of the weld metal to a thickness of 10 mm. All weld metals were formed by covered arc welding. From the results of test numbers 1 to 24, the components of the hardfacing metal to improve the wear resistance of the hammer are: C: 5.0 to 6.0%, Cr: 20 to 30%,
Nb: 2.0-8.0%, Mo: 0.3-6.0%, W: 2.0-5.0
%, V: 0.2 to 3.0%, with the balance consisting of iron and unavoidable impurities. In test numbers 25 to 27, hardened overlay metal was formed directly on the fracture surface of the hammer, but peeling cracks occurred in all cases, indicating that underlaying with austenitic stainless steel SUS309 was required. It can be done. In test numbers 28 to 29, the thickness of the hardfacing metal was changed to 15 mm, 20 mm, and 23 mm, respectively.
If the thickness of hardfacing metal exceeds 20 mm, peeling cracks will occur. Further, if the thickness of the hardfacing metal is not 5 mm or more, the hardness will be insufficient due to the influence of the base material, so the appropriate thickness of the hardfacing metal is 5 to 20 mm. [Effects of the invention] The present invention improves wear resistance by using the highly hard crystallized carbides of the high-carbon, high-chromium hardfacing weld metal formed on the fracture surface of the steel hammer. Also,
The austenitic stainless steel formed between the hammer base material and the hardfacing weld metal prevents peeling cracks in the hardfacing weld metal.
【表】【table】
【表】【table】
【表】
（注）上記化学成分は標記した化学成分値の他
はFe及び不可避的不純物よりなる。[Table] (Note) The above chemical components consist of Fe and unavoidable impurities in addition to the chemical component values listed.
第１図は本考案に係る一実施例の側断面図、第
２図は従来のクラツシヤの側面図、第３図は従来
のハンマの使用後の状況を示す側断面図である。
１：ハンマ本体、１ａ：SUS309溶接金属、１
ｂ：硬化肉盛金属。
FIG. 1 is a side sectional view of one embodiment of the present invention, FIG. 2 is a side view of a conventional crusher, and FIG. 3 is a side sectional view showing the state of the conventional hammer after use. 1: Hammer body, 1a: SUS309 weld metal, 1
b: Hardened overlay metal.
Claims (1)
いて、上記ハンマ破砕面にオーステナイト系ステ
ンレス鋼の溶接金属を形成した上に化学成分が、
重量パーセントでｃ：5.0〜6.0％、Cr：20〜30
％、Nb：2.0〜8.0％、Mo：0.3〜6.0％、Ｗ：2.0
〜5.0％、Ｖ：0.2〜3.0％、残部を鉄及び不可避的
不純物となる溶接金属を厚さが５mm以上、20mm以
下の範囲で形成させたことを特徴とするクラツシ
ヤハンマ。 In the crusher hammer that crushes coal and rocks, weld metal of austenitic stainless steel is formed on the crushing surface of the hammer, and the chemical composition is
In weight percentage c: 5.0~6.0%, Cr: 20~30
%, Nb: 2.0-8.0%, Mo: 0.3-6.0%, W: 2.0
5.0%, V: 0.2 to 3.0%, the balance being iron and weld metal as unavoidable impurities with a thickness in the range of 5 mm or more and 20 mm or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7910585U JPH0334278Y2 (en) | 1985-05-27 | 1985-05-27 |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7910585U JPH0334278Y2 (en) | 1985-05-27 | 1985-05-27 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61195348U JPS61195348U (en) | 1986-12-05 |
| JPH0334278Y2 true JPH0334278Y2 (en) | 1991-07-19 |
Family
ID=30623703
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7910585U Expired JPH0334278Y2 (en) | 1985-05-27 | 1985-05-27 |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0334278Y2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5048965B2 (en) * | 2006-04-19 | 2012-10-17 | 新日本製鐵株式会社 | Hammer head |
-
1985
- 1985-05-27 JP JP7910585U patent/JPH0334278Y2/ja not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61195348U (en) | 1986-12-05 |
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