JPH03248799A - Roll for steelmaking - Google Patents
Roll for steelmakingInfo
- Publication number
- JPH03248799A JPH03248799A JP4830390A JP4830390A JPH03248799A JP H03248799 A JPH03248799 A JP H03248799A JP 4830390 A JP4830390 A JP 4830390A JP 4830390 A JP4830390 A JP 4830390A JP H03248799 A JPH03248799 A JP H03248799A
- Authority
- JP
- Japan
- Prior art keywords
- roll
- weight
- coating layer
- steelmaking
- hardness
- 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
- 238000009628 steelmaking Methods 0.000 title claims abstract description 20
- 239000011247 coating layer Substances 0.000 claims abstract description 32
- 239000000843 powder Substances 0.000 claims abstract description 29
- 239000000463 material Substances 0.000 claims abstract description 23
- 229910000640 Fe alloy Inorganic materials 0.000 claims abstract description 13
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 claims abstract description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910000831 Steel Inorganic materials 0.000 claims description 5
- 239000010959 steel Substances 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 239000000203 mixture Substances 0.000 abstract description 12
- 238000005496 tempering Methods 0.000 abstract description 11
- 238000000034 method Methods 0.000 abstract description 8
- 239000010410 layer Substances 0.000 abstract description 7
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 150000001247 metal acetylides Chemical class 0.000 description 11
- 230000007423 decrease Effects 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 238000003466 welding Methods 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000005496 eutectics Effects 0.000 description 3
- 238000005087 graphitization Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 238000009689 gas atomisation Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- PEDCQBHIVMGVHV-UHFFFAOYSA-N Glycerine Chemical compound OCC(O)CO PEDCQBHIVMGVHV-UHFFFAOYSA-N 0.000 description 1
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical group C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000007750 plasma spraying Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 235000012239 silicon dioxide Nutrition 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
- Powder Metallurgy (AREA)
- Coating By Spraying Or Casting (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、熱間圧延用ロール、搬送用ロール等の製鋼用
ロールに間する。詳細には、高温下ここざらされても硬
度が低下しない、高温耐摩耗性の被覆層が形成されてい
る製鋼用ロールに間する。DETAILED DESCRIPTION OF THE INVENTION (Industrial Field of Application) The present invention relates to rolls for steel manufacturing such as hot rolling rolls and conveying rolls. Specifically, the steelmaking roll has a high-temperature wear-resistant coating layer that does not reduce its hardness even when exposed to high temperatures.
（従来の技術）
製鋼用ロールとしては、十分な硬度と耐摩耗性が要求さ
れる。特に、熱間圧延加工に供されるロールにあっては
、高い熱と圧力とが加わるため、より高い硬度と耐摩耗
性とが要求される。(Prior Art) Steelmaking rolls are required to have sufficient hardness and wear resistance. In particular, rolls used for hot rolling are required to have higher hardness and wear resistance because high heat and pressure are applied to them.
従来の製鋼用ロールとしては、特閘昭６３−１９９０９
２号公報に記載されたものがある。As a conventional steelmaking roll, Tokusho 63-19909
There is one described in Publication No. 2.
この製鋼用ロールは、靭性を有する鋼材りこよるロール
芯部の外周に、プラズマ粉体溶接によって肉盛層が形成
され、この肉盛層はその組成が重量％て、
Ｃ： １．５〜２．５ ％、Ｓｉ：０．１〜１．５
％、Ｍ ｎ ： ０．１〜１．０ ％、Ｎ ｉ
： ０．１〜１．５ ％、Ｃｒ ： １．０〜５．０
％、Ｍ ｏ ： １．０〜５．０ ％、Ｃｏ：
５．０−１５．０％、Ｗ ： ５．０〜１５．０％、
Ｖ：６．Ｏ〜１５．０％、
及び残部実質的にＦｅからなることを特徴とするもので
ある。This steelmaking roll has a build-up layer formed by plasma powder welding on the outer periphery of a roll core made of tough steel, and the composition of this build-up layer is 1.5 to 2 by weight. .5%, Si: 0.1-1.5
%, Mn: 0.1-1.0%, Ni
: 0.1~1.5%, Cr: 1.0~5.0
%, Mo: 1.0-5.0%, Co:
5.0-15.0%, W: 5.0-15.0%,
V:6. O~15.0%, and the remainder substantially consists of Fe.
（発明が解決しようとする課題）
製鋼用ロールの硬度及び耐摩耗性は、ロール外層におけ
るＣ含有量に依存している。(Problems to be Solved by the Invention) The hardness and wear resistance of a steelmaking roll depend on the C content in the outer layer of the roll.
ところが、上記製鋼用ロールにあっては、そのＣ含有量
カ月、５〜２．５重量％であり、硬度及び耐摩耗性とい
う点では不十分なものであった。このため、長期に渡っ
て使用するにつれてロール表面が摩耗し、逐次ロールの
取り替えを必要としていた。However, in the above steelmaking roll, the C content was 5 to 2.5% by weight, which was insufficient in terms of hardness and wear resistance. For this reason, the roll surface wears out as the roll is used over a long period of time, making it necessary to replace the roll from time to time.
該製鋼用ロールの被覆層の硬度及び耐摩耗性は、Ｃ含有
量を増やすことによって向上させることができるのであ
るが、この場合、高温で焼き戻したとき、生成炭化物が
粗大化して、ロール外層における炭素を含むセメンタイ
ト組織の体積分布が小さくなり、この結果、外層の硬度
及び耐摩耗性が著しく低下するという事態を招いていた
。The hardness and abrasion resistance of the coating layer of the steelmaking roll can be improved by increasing the C content, but in this case, when tempered at high temperature, the formed carbide becomes coarse and the outer layer of the roll deteriorates. The volume distribution of the carbon-containing cementite structure becomes smaller, resulting in a significant decrease in the hardness and wear resistance of the outer layer.
本発明は、上記事情に鑑みなされたものであり、高温下
にさらされても硬度が低下しない、高温耐摩耗性の被覆
層が形成されている製鋼用ロールを提供することを目的
とするものである。The present invention was made in view of the above circumstances, and an object of the present invention is to provide a steelmaking roll having a high-temperature wear-resistant coating layer that does not reduce its hardness even when exposed to high temperatures. It is.
（課題を解決するための手段及び作用）上記目的を達成
するため、本発明にあっては、以下に示す■〜■の組成
の高炭素鉄合金の急冷凝固粉末材料による被覆層が形成
されていることを特徴とする製鋼用ロールをその要旨と
した。(Means and effects for solving the problem) In order to achieve the above object, in the present invention, a coating layer is formed of a rapidly solidified powder material of a high carbon iron alloy having the compositions shown below. The gist of this paper is a steelmaking roll that is characterized by the following characteristics:
■： Ｃ：３．５〜６．０重量％、 Ｍｏ： Ｃｒ： Ｆ ｅ： ■： Ｃ： Ｍｏ二 Ｃｒ二 Ｃｏ： Ｆ ｅ： ■： ３．０〜１０．０重量％、 ５．０〜１５．０重量％、 残部。■： C: 3.5 to 6.0% by weight, Mo: Cr: F e: ■： C: Mo2 Cr2 Co: F e: ■： 3.0-10.0% by weight, 5.0-15.0% by weight, The rest.
３．５〜６．０重量％、
３．０〜１０．０重量％、
５．０〜１５．０重量％、
５．０〜１５．０重量％及びＮ ｉ ： ５．０〜２０
．０重量％のうち少なくとも一方を含み、
残部。3.5-6.0 wt%, 3.0-10.0 wt%, 5.0-15.0 wt%, 5.0-15.0 wt% and Ni: 5.0-20
．． 0% by weight, and the remainder.
■：
まず、
■若しくは■に対し、Ｖ１．０−１０．０重量％及びＷ
１．０〜１５ 、帽１ ％のうち少なくとも一方を含む
、
■、■若しくは■に対し、Ｓ ｉ Ｏ，５〜２．０重量
％及びＡ Ｑ ０．５〜５．０重量％のうち少なくとも
一方を含む。■: First, for ■ or ■, V1.0-10.0% by weight and W
1.0 to 15%, and 1% to 1.0 to 15% by weight; Including one.
■の高炭素鉄合金の急冷凝固粉末材料について説明する
。The rapidly solidified powder material of high carbon iron alloy (2) will be explained.
Ｃは、炭化物形成元素であるＭｏ及びＣｒとの間で炭化
物を形成してロール表面の被覆層の硬度を向上せしめる
元素である。高炭素鉄合金中のＣ量は、３．５〜６．０
重量％である必要がある。というのは、Ｃ量が３．５重
量％未満ては形成される炭化物量が少なくなり、被覆層
の硬度が不足することになる。一方、Ｃ量が６．０重量
％を超えると被覆層の靭性が低下するからである。C is an element that forms carbides with Mo and Cr, which are carbide-forming elements, and improves the hardness of the coating layer on the roll surface. The amount of C in high carbon iron alloy is 3.5 to 6.0
Must be in weight%. This is because if the amount of C is less than 3.5% by weight, the amount of carbides formed will be small and the hardness of the coating layer will be insufficient. On the other hand, if the amount of C exceeds 6.0% by weight, the toughness of the coating layer will decrease.
Ｃｒは、Ｃとの間で炭化物を形成して、ロールの被覆層
の硬度を向上させる元素である。このＣｒ量は５．０〜
１５．０重量％である必要がある。というのは、Ｃｒ量
が５．０重量％未満では６００℃以上の焼き戻しで炭化
物の粗大化が起こり、被覆層の硬度が低下する。一方、
ＣｒＪｌカ月５．０重量％を超えても、被覆層の硬度及
び焼き戻し軟化抵抗は変わらない反面、 （Ｆ ｅ 、
Ｃｒ ） ？Ｃ３なる炭化物が生成され脆くなるからで
ある。Cr is an element that forms carbides with C to improve the hardness of the coating layer of the roll. This Cr amount is 5.0~
It needs to be 15.0% by weight. This is because if the Cr content is less than 5.0% by weight, carbides become coarser when tempered at 600° C. or higher, and the hardness of the coating layer decreases. on the other hand,
Even if the CrJl content exceeds 5.0% by weight per month, the hardness and tempering softening resistance of the coating layer remain the same; however, (F e ,
Cr)? This is because a carbide called C3 is generated and becomes brittle.
Ｍｏは、Ｃとの間で炭化物を形成して、ロールの被覆層
の硬度を向上せしむるとともに靭性を向上させ、更には
、６００℃以上の焼き戻し時における炭化物の粗大化を
抑制する機能を有する元素である。Ｍｏの働きのうち特
に高温での焼き戻し時における炭化物の粗大化を抑制す
る機能を十分に発揮せしめるため、Ｍ ｏ Ｉｔが３．
０重量％以上である必要がある。一方、Ｍｏの添加効果
は、１０．０重量％で飽和化し、それ以上の量を添加し
ても上記機能の向上はなく、又、コストの面から１００
０重量％が上限である。Mo forms carbides with C to improve the hardness and toughness of the coating layer of the roll, and also has the function of suppressing coarsening of carbides during tempering at 600°C or higher. It is an element with Among the functions of Mo, in particular, in order to fully exhibit the function of suppressing coarsening of carbides during tempering at high temperatures, Mo It is set to 3.
It needs to be 0% by weight or more. On the other hand, the effect of adding Mo is saturated at 10.0% by weight, and adding more than that does not improve the above-mentioned functions.
0% by weight is the upper limit.
次に、■の組成を有する高炭素鉄合金の急冷凝固粉末材
料について説明する。Next, a rapidly solidified powder material of a high carbon iron alloy having the composition (2) will be explained.
■の粉末材料は、■の粉末材料に、更にＣＯ及び又はＮ
ｉを含有せしめたものである。The powder material (2) is added to the powder material (2) with CO and/or N.
It contains i.
Ｃｏは、ロールの被覆層の硬度及び焼き戻し軟化抵抗に
対しては殆ど影響はなく、被覆層の靭性を向上させる元
素である。ＣＯ添加量は５．０重量％未満ては被覆層の
靭性を向上させる機能は不十分である。一方、ＣＯ添加
量カ月５．０重量％を超えると、８００℃以上で焼き戻
したとき、炭化物の分解を促進し、結果的に被覆層の硬
度を低下させるので１５．０重量％が上限となる。Co has almost no effect on the hardness and temper softening resistance of the coating layer of the roll, and is an element that improves the toughness of the coating layer. If the amount of CO added is less than 5.0% by weight, the function of improving the toughness of the coating layer is insufficient. On the other hand, if the amount of CO added exceeds 5.0% by weight per month, it will promote the decomposition of carbides when tempered at 800°C or higher, resulting in a decrease in the hardness of the coating layer, so 15.0% by weight is the upper limit. Become.
Ｎ１は、耐食性、特に酸乞こ対する耐食性を向上させる
元素である。その添加量は５．０重量％未満ては上記性
能が発現されず、２０．０重量％を超えると、被覆層の
硬度の低下と共に焼き戻し軟化抵抗をも低下するので、
Ｎｉ量は５．０〜２０．０重量％の範囲となる。N1 is an element that improves corrosion resistance, particularly resistance to acid corrosion. If the amount added is less than 5.0% by weight, the above performance will not be achieved, and if it exceeds 20.0% by weight, the hardness of the coating layer will decrease and the tempering softening resistance will also decrease.
The amount of Ni is in the range of 5.0 to 20.0% by weight.
尚、ＣｏとＮ１とをともに添加する場合、これらを併せ
た添加量が２５．０重量％以下であることが好ましい。In addition, when both Co and N1 are added, it is preferable that the combined amount of these added is 25.0% by weight or less.
次に、■の組成を有する高炭素鉄合金の急冷凝固粉末材
料について説明する。Next, a rapidly solidified powder material of a high carbon iron alloy having the composition (2) will be explained.
■の粉末材料は、■若しくは■の粉末材料に、更にＶ及
び又はＷを含有せしめたものである。The powder material (2) is obtained by adding V and/or W to the powder material (2) or (2).
■及びＷは、共に強い炭化物形成元素であり、被覆層の
硬度を向上させる効果があり、特にＣｏ、Ｎｉ存在下で
は、高温での焼き戻し時における黒鉛化防止に有効であ
る。このＶ及びＷの添加効果は、いずれも１．０重量％
未満では顕著なものではない。逆に、Ｖ量は１０００重
量％、Ｗ量は１５．０重量％を超えると、ロールの被覆
層の靭性が低下するため、各々１０００重量％、１５．
０重量％が上限となる。(2) and W are both strong carbide-forming elements, and have the effect of improving the hardness of the coating layer. Particularly in the presence of Co and Ni, they are effective in preventing graphitization during tempering at high temperatures. The effect of adding V and W is both 1.0% by weight.
Less than that is not noticeable. On the other hand, if the amount of V exceeds 1000% by weight and the amount of W exceeds 15.0% by weight, the toughness of the coating layer of the roll decreases.
The upper limit is 0% by weight.
次に、■の組成を有する高炭素鉄合金の急冷凝固粉末材
料について説明する。Next, a rapidly solidified powder material of a high carbon iron alloy having the composition (2) will be explained.
■の組成の粉末材料は、■、■若しくは■の粉末材料に
、更にＳｉ及び又はＡＱを含有せしめたものである。The powder material having the composition (2) is obtained by adding Si and/or AQ to the powder material (2), (2) or (2).
Ｓｉ及びＡ２は、ロールが高温大気中に曝された場合に
、５１０２、Ａｇ２Ｏ３なる緻密な酸化被膜を形成して
、より以上の高温酸化を防止することから、耐熱性及び
耐久性を高める一方、Ｓｉは強い、ＡＱは弱くはあるが
、いずれも黒鉛化促進傾向を持つために、あまり多量に
入れると、被覆層の硬度を低下させることになる。この
ため、Ｓｌにあっては、０．５〜２．０重量％、Ａ２ζ
こあっては、０．５〜５．０重量％の範囲で添加するの
が好ましい。Si and A2 form a dense oxide film of 5102, Ag2O3 when the roll is exposed to the high temperature atmosphere and prevent further high temperature oxidation, so while increasing heat resistance and durability, Although Si is strong and AQ is weak, both have a tendency to promote graphitization, so if too large a quantity is added, the hardness of the coating layer will be reduced. Therefore, for Sl, 0.5 to 2.0% by weight, A2ζ
In this case, it is preferable to add it in an amount of 0.5 to 5.0% by weight.
本発明の高炭素鉄合金の急冷凝固粉末材料は、ガスアト
マイズ法等の急冷凝固粉末生成法によって生成され、そ
の粒径は１０〜２００μｍである。また、急冷凝固した
ままの組織は、平衡固溶限以上の固溶原子を含む過飽和
固溶体と、均一に分散した微細な炭化物とからなってお
り、これを８００℃以上の高温で焼き戻した場合でも、
炭化物の大きさに余り大きな変化がみられず、高い硬度
と耐摩耗性を保持しているものと考えられる。The rapidly solidified powder material of the high carbon iron alloy of the present invention is produced by a rapidly solidified powder production method such as a gas atomization method, and has a particle size of 10 to 200 μm. In addition, the structure that remains rapidly solidified consists of a supersaturated solid solution containing solute atoms above the equilibrium solid solubility limit and fine carbides uniformly dispersed, and when this is tempered at a high temperature of 800°C or higher, but,
There was no significant change in the size of the carbide, which suggests that it maintains high hardness and wear resistance.
この粉末材料を用い、肉盛溶接法、熱間静水り成形法（
）ＩＩＰ法）、溶射法なとの従来より知られた被覆層を
形成する方法によって、ロール表面に被覆層が形成され
ているのである。Using this powder material, overlay welding method, hot still water forming method (
The coating layer is formed on the roll surface by conventionally known coating layer forming methods such as ) IIP method) and thermal spraying method.
′ＬＩＬｆＩＪ１ 試料Ｎ。'LILfIJ1 Sample N.
組成
（重量％）
ガスアトマイズ法によって上記試料Ｎｏ１〜６に示す組
成の急冷凝固粉末材料を生成し、この粉末材料を用い、
熱間搬送用ロールの表面に、１３５Ａ、３４Ｖ、送り速
度７０ｍｍ＃ｎ ｉｎ、粉末送り量的１２３／ｍｉｎな
る条件でプラズマ粉体肉盛溶接をした。ロール表面の溶
接部の硬度と、それを１０００℃までの各温度で５時間
焼き戻した後の硬度の変化を第１図に示す。Composition (wt%) Rapidly solidified powder materials having the compositions shown in Samples Nos. 1 to 6 above are produced by the gas atomization method, and using this powder material,
Plasma powder overlay welding was performed on the surface of the hot conveyance roll under the following conditions: 135A, 34V, feed rate 70 mm #n in, and powder feed amount 123/min. Figure 1 shows the hardness of the welded part on the roll surface and the change in hardness after tempering it at various temperatures up to 1000°C for 5 hours.
又、試料Ｎｏｌを６００℃×１時閏の加熱処理したもの
の組織を第２図に、試料Ｎｏｌを８００℃×１時間の加
熱処理したものの組織を第３図にそれぞれ顕微鏡組織写
真で示す。これら第２図及び第３図の倍率は共に１００
倍である。この顕微鏡組織写真から６００℃×１時間の
加熱処理したものは、初晶炭化物とレデブライト共晶か
らなっており、共晶組織が非常に微細であり、炭化物が
均一微細に分散されていることが判る。また、８００℃
×１時閏の加熱処理をしたものの組織においても殆ど変
化がないことが判る。Further, FIG. 2 shows the microstructure of sample No. 1 heated at 600° C. for 1 hour, and FIG. 3 shows the structure of sample No. 1 heated at 800° C. for 1 hour as microscopic micrographs. The magnification of both Figures 2 and 3 is 100.
It's double. From this microscopic structure photograph, it can be seen that the material heated at 600°C for 1 hour consists of primary carbide and ledebrite eutectic, and the eutectic structure is very fine, and the carbides are uniformly and finely dispersed. I understand. Also, 800℃
It can be seen that there is almost no change in the structure even after the heat treatment of ×1 time.
寛厳■ユ
試料Ｎ ｏ ？ ［Ｃ：５−０．Ｃｒ：１０−０．Ｍｏ
：５．０．Ｓｉ：１．０．Ａｆｌ：］、０．Ｆｅ：残部
（重量％）］の組成の粉末材料を用い、直径３００ｍｍ
、 長さ９００ｍｍの胴部を有する熱間金属材運搬用
ロールの表面に、実施例１と同様の条件のプラズマ粉体
肉盛溶接で層厚５ｍ＋ｎとなる様に溶着し、従来のこの
種のロールである高Ｃ「鋼製ロールと共に、同条件下で
６力月閏の実機テストを行った。Gentle ■Yu sample No? [C:5-0. Cr:10-0. Mo
:5.0. Si:1.0. Afl: ], 0. Using a powder material with a composition of [Fe: balance (weight %)], the diameter was 300 mm.
, Welded a layer thickness of 5m+n to the surface of a roll for transporting hot metal materials having a body part of 900mm in length by plasma powder deposition welding under the same conditions as in Example 1. We conducted an actual machine test of the six power moon leap under the same conditions together with the high C steel roll.
この結果を第１表に示す。The results are shown in Table 1.
試料Ｎｏ７を用いた溶接部の高温時での６力月間使用し
た後のロールの写真を第４図に示す。FIG. 4 shows a photograph of the roll after 6 months of use at a high temperature of the welded part using sample No. 7.
支鞭土ユ
ガスアトマイズ法によって実施例２で使用した試料Ｎｏ
７の組成の急冷凝固粉末材料を生成し、この粉末材料を
用い、試験片（５０■Ｘ１０ｔ）の表面に、プラズマ粉
体肉盛溶接及びプラズマ溶射によってそれぞれ被覆層を
形成する。そして、これらの試験片を、第５図に示すよ
うに、５４５Ｃよりなる相手片（１９０■Ｘ１０ｔ）に
摺合わせ状態に設け、試験片を５５０℃の温度とし、３
０ｋｇの荷重をかけつつ３００ｒｐｍの速度で回転させ
る。一方、相手片にあっても９００℃の温度とし、３０
ｋｇの荷重をかけつつ１１００ｒｐの速度で回転させ、
各試験片の被覆層の摩耗量（ｍｇ）を測定した。Sample No. used in Example 2 by the chinoflagellate Yugas atomization method
A rapidly solidified powder material having the composition No. 7 was produced, and using this powder material, a coating layer was formed on the surface of a test piece (50 mm x 10 tons) by plasma powder overlay welding and plasma spraying, respectively. Then, as shown in Fig. 5, these test pieces were placed in a sliding state on a mating piece (190 x 10t) made of 545C, and the temperature of the test piece was set to 550°C.
Rotate at a speed of 300 rpm while applying a load of 0 kg. On the other hand, the temperature of the other piece is 900℃, and the temperature is 30℃.
Rotate at a speed of 1100 rpm while applying a load of kg,
The amount of wear (mg) of the coating layer of each test piece was measured.
又、上記試験片の他に、ステライ） Ｎｏ６を用い、試
験片の表面にプラズマ粉体肉盛溶接によって被覆層を形
成したものや、チッ化鋼（ＳＡＣＭ６４５）を用いたも
ので、同様に試験を行った。In addition to the above-mentioned test pieces, test pieces using Stellai No. 6 with a coating layer formed on the surface of the test piece by plasma powder build-up welding, and those using nitrided steel (SACM645) were also tested in the same way. I did it.
この結果を第６図に示す。第６図から試料Ｎｏ７の組成
の粉末材料を用いたものは、高温での焼き戻しても軟化
しないことが判る。これは炭素含有量が高いため、また
、Ｃｒ及びＭｏの添加により、炭化物及びレデブライト
共晶が成長しないためと考えられる。The results are shown in FIG. It can be seen from FIG. 6 that the powder material having the composition of Sample No. 7 does not soften even when tempered at a high temperature. This is considered to be because the carbon content is high, and because carbides and ledebrite eutectic do not grow due to the addition of Cr and Mo.
（発明の効果）
以上述べた如く、請求項１記載の発明の製鋼用ロールに
よれば、被覆されたままのロールの被覆層の硬度は、Ｓ
ＫＤ、 ＳＫＳあるいは高速度鋼を用いた被膜のそれ
と略同じであり、その後の高温焼き戻しでは、上記従来
品が急速にその硬度を低下させるのに対し、本発明のロ
ールの被覆層は高温焼き戻し処理を施しても硬度の低下
は殆どみられ無い。(Effects of the Invention) As described above, according to the steelmaking roll of the invention set forth in claim 1, the hardness of the coating layer of the roll as it is coated is S
This is almost the same as that of a coating made using KD, SKS or high-speed steel, and while the conventional product described above rapidly loses its hardness after subsequent high-temperature tempering, the coating layer of the roll of the present invention does not undergo high-temperature tempering. Even after the return treatment, there is almost no decrease in hardness.
又、従来の製鋼用ロールに比へ、ロール表面の摩耗をよ
り低く抑えることができ、ロールの取り替え頻度を少な
くすることができる。Furthermore, compared to conventional steelmaking rolls, wear on the roll surface can be suppressed to a lower level, and the frequency of roll replacement can be reduced.
請求項２記載の製鋼用ロールによれば、ロール表面の被
覆層の靭性及び又は耐食性を更に向上せしめることがで
きる。According to the steelmaking roll according to the second aspect, the toughness and/or corrosion resistance of the coating layer on the roll surface can be further improved.
請求項３記載の製鋼用ロールによれば、ロール表面の被
覆層の硬度をより向上させることができ、特にＣｏ、Ｎ
】存在下ては、高温での焼き戻し時における黒鉛化を防
止することができる。According to the steelmaking roll according to claim 3, the hardness of the coating layer on the roll surface can be further improved, and in particular Co, N
] In its presence, graphitization during tempering at high temperatures can be prevented.
請求項４記載の製鋼用ロールによれば、該製鋼用ロール
が高温大気中にさらされた場合でも、ＳｉＯ２、Ａ１１
２０３なる緻密な酸化被膜を形成して、ロール表面の被
覆層の高温酸化を防止し、耐酸化性及び耐久性を高める
ことができる。According to the steelmaking roll according to claim 4, even when the steelmaking roll is exposed to high temperature atmosphere, SiO2, A11
By forming a dense oxide film of 203, it is possible to prevent high-temperature oxidation of the coating layer on the roll surface and improve oxidation resistance and durability.
第１図は実施例１の焼き戻し温度の変化に伴う硬度の変
化を示すグラフ、第２図は試料Ｎｏｌを６００℃×１時
間の加熱処理したものの顕微鏡組織写真、第３図は試料
Ｎｏｌを８００℃×１時閏の加熱処理したものの顕微鏡
組織写真、第４図は実施例２の試料Ｎｏ７を用いた溶接
部の高温時での６力月間使用後のロールの拡大写真、第
５図は実施例３の試験装置を示した模式図、第６図は実
施例３における試験片の摩耗量（ｍ８）と回転数との関
係を示したグラフである。
第１図
、Ｎｏ、６
第２図
第ご（１〈
ＸりＱノゼｔ
第
５
図
第６図
回Ｒ数（町Figure 1 is a graph showing changes in hardness with changes in tempering temperature in Example 1, Figure 2 is a microscopic structure photograph of sample No. 1 heated at 600°C for 1 hour, and Figure 3 is a graph of sample No. A microscopic structure photograph of the product heat-treated at 800°C x 1 hour, Figure 4 is an enlarged photograph of the welded part using sample No. 7 of Example 2 after 6 months of use at high temperature, and Figure 5 is an enlarged photograph of the roll after use for 6 months. FIG. 6 is a schematic diagram showing the test apparatus of Example 3, and a graph showing the relationship between the amount of wear (m8) of the test piece and the rotation speed in Example 3. Figure 1, No. 6 Figure 2 (1〈
Claims (4)
に、炭化物形成元素であるＭｏとＣｒとが含まれており
、その含有量がＭｏ３．０〜１０．０重量％、Ｃｒ５．
０〜１５．０重量％である高炭素鉄合金の急冷凝固粉末
材料による被覆層が形成されていることを特徴とする製
鋼用ロール。(1) Contains 3.5 to 6.0% by weight of C in addition to Fe, and further contains Mo and Cr, which are carbide forming elements, and the content is Mo3.0 to 10.0% by weight. , Cr5.
A roll for steelmaking, characterized in that a coating layer is formed with a rapidly solidified powder material of a high carbon iron alloy in an amount of 0 to 15.0% by weight.
％及びＮｉ５．０〜２０．０重量％のうち少なくとも一
方が含まれていることを特徴とする請求項１記載の製鋼
用ロール。(2) The steel manufacturing method according to claim 1, wherein the high carbon iron alloy contains at least one of 5.0 to 15.0% by weight of Co and 5.0 to 20.0% by weight of Ni. roll.
．０〜１０．０重量％及びＷ１．０〜１５．０重量％の
うち少なくとも一方が含まれていることを特徴とする請
求項１又は２記載の製鋼用ロール。(3) In the high carbon iron alloy, V1 is added as a carbide forming element.
．． The steelmaking roll according to claim 1 or 2, characterized in that it contains at least one of 0 to 10.0% by weight and 1.0 to 15.0% by weight of W.
及びＡｌ０．５〜５．０重量％のうち少なくとも一方が
含まれていることを特徴とする請求項１、２又は３記載
の製鋼用ロール。(4) Si0.5 to 2.0% by weight in the high carbon iron alloy
The steelmaking roll according to claim 1, 2 or 3, wherein at least one of 0.5 to 5.0% by weight of Al is contained.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4830390A JPH03248799A (en) | 1990-02-27 | 1990-02-27 | Roll for steelmaking |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4830390A JPH03248799A (en) | 1990-02-27 | 1990-02-27 | Roll for steelmaking |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03248799A true JPH03248799A (en) | 1991-11-06 |
Family
ID=12799664
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4830390A Pending JPH03248799A (en) | 1990-02-27 | 1990-02-27 | Roll for steelmaking |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03248799A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018094573A (en) * | 2016-12-09 | 2018-06-21 | 新日鐵住金株式会社 | Method of forming discharge treatment membrane |
| CN109371396A (en) * | 2018-12-27 | 2019-02-22 | 安徽工业大学 | A kind of big thickness cold roll laser restorative procedure of high-carbon stiff dough flawless |
| JP2019513083A (en) * | 2016-03-22 | 2019-05-23 | スコペルタ・インコーポレイテッドＳｃｏｐｅｒｔａ， Ｉｎｃ． | Fully readable thermal spray coating |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
-
1990
- 1990-02-27 JP JP4830390A patent/JPH03248799A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2019513083A (en) * | 2016-03-22 | 2019-05-23 | スコペルタ・インコーポレイテッドＳｃｏｐｅｒｔａ， Ｉｎｃ． | Fully readable thermal spray coating |
| US11279996B2 (en) | 2016-03-22 | 2022-03-22 | Oerlikon Metco (Us) Inc. | Fully readable thermal spray coating |
| JP2018094573A (en) * | 2016-12-09 | 2018-06-21 | 新日鐵住金株式会社 | Method of forming discharge treatment membrane |
| US11939646B2 (en) | 2018-10-26 | 2024-03-26 | Oerlikon Metco (Us) Inc. | Corrosion and wear resistant nickel based alloys |
| CN109371396A (en) * | 2018-12-27 | 2019-02-22 | 安徽工业大学 | A kind of big thickness cold roll laser restorative procedure of high-carbon stiff dough flawless |
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