EP0510598B1 - Cylindre composite résistant à l'usure - Google Patents

Cylindre composite résistant à l'usure Download PDF

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Publication number
EP0510598B1
EP0510598B1 EP19920106860 EP92106860A EP0510598B1 EP 0510598 B1 EP0510598 B1 EP 0510598B1 EP 19920106860 EP19920106860 EP 19920106860 EP 92106860 A EP92106860 A EP 92106860A EP 0510598 B1 EP0510598 B1 EP 0510598B1
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EP
European Patent Office
Prior art keywords
roll
carbide particles
wear
compound
compound roll
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
Application number
EP19920106860
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German (de)
English (en)
Other versions
EP0510598A2 (fr
EP0510598A3 (en
Inventor
Takuya Ohsue
Akira Noda
Hiroshi Fukuzawa
Itsuo Korenaga
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Hitachi Metals Ltd
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Filing date
Publication date
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Publication of EP0510598A2 publication Critical patent/EP0510598A2/fr
Publication of EP0510598A3 publication Critical patent/EP0510598A3/en
Application granted granted Critical
Publication of EP0510598B1 publication Critical patent/EP0510598B1/fr
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/06—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools
    • B22F7/08—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools with one or more parts not made from powder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon

Definitions

  • the present invention relates to a wear-resistant compound roll, and more particularly to a wear-resistant compound roll having a shell portion formed around a core portion, the shell portion being made of a sintered alloy material showing excellent wear resistance.
  • the rolls are required to have roll surfaces suffering from little wear, little surface roughening, little sticking with materials being rolled, less cracks and fractures, etc.
  • cast compound rolls having hard outer surfaces and forged steel rolls having roll body portions hardened by heat treatment, etc. are conventionally used.
  • various materials and production methods are used for preparing these rolls.
  • JP-A-62-7802 discloses a compound roll constituted by a shell portion and a roll core, the shell portion being made from powder of a high-speed steel, a high-Mo cast iron, a high-Cr cast iron, a Ni-Cr alloy, etc., and diffusion-bonded to the roll core by a HIP treatment.
  • JP-A-58-128525 discloses a cemented carbide roll and a compound ring roll whose ring portion is made of a cemented carbide.
  • JP-A-58-87249 discloses a wear-resistant cast roll having a composition consisting essentially of 2.4-3.5% of C, 0.5-1.3% of Si, 0.3-0.8% of Mn, 0-3% of Ni, 2-7% of Cr, 2-9% of Mo, 0-10% of W, 6-14% of V, and balance Fe and inevitable impurities.
  • W, Mo and V form metal carbides, contributing to providing the roll with excellent wear resistance.
  • this roll material is produced by casting, it still suffers from the problems that the particle sizes of metal carbides are as large as 50-200 ⁇ m, and that the distribution of the metal carbides is microscopically not uniform.
  • JP-A-1252704 discloses a wear-resistant compound roll produced by a HIP process.
  • JP-A-2-270944 discloses a wear-resistant and surface-roughening resistant one-piece roll produced by subjecting an alloy powder consisting of, by weight, 1.2 - 3.5 % of C, 3 - 6 % of Cr, 4 - 10 % of Mo, 2 - 15 % of W, 2 - 10 % of V 1 - 15 % of Co and balance of inevitable impurities and Fe to hot isostatic press, said roll containing 5 - 40 % by area of carbides of 25 - 100 ⁇ m particle size and having no powdery areas of alloy in the matrix.
  • An object of the present invention is, accordingly, to provide a wear-resistant compound roll having a shell portion made of a sintered alloy showing excellent wear resistance.
  • the wear-resistant compound roll according to the present invention has a shell portion produced by sintering an alloy powder comprising, by weight, 1.0-3.5% of C, 0,2-1% of Si, 0,2-1% of Mn, 10% or less of Cr, 3-15% of W, 2-10% of Mo, 1-15% of V, optionally 3-15% of Co, and balance Fe and inevitable impurities, the shell portion containing carbide particles having particle sizes within the range of 3-50 ⁇ m in a martensite or bainite matrix, and an area ratio of the carbide particles in the metal structure of the sintered shell portion being 15% or more, wherein among the carbide particles having particle sizes of 0.5 ⁇ m or more, the number of the carbide particles having particle sizes of 3 ⁇ m or more is 10% or more.
  • the alloy powder used for producing the shell portion of the compound loll in the present invention has a composition comprising, by weight, 1.0-3.5% of C, 0,2-1% of Si, 0,2-1% of Mn, 10% or less of Cr, 3-15% of W, 2-10% of Mo, 1-15% of V, optionally 3-15% of Co, and balance Fe and inevitable impurities.
  • C is combined with Cr, W, Mo and V to form hard carbides, contributing to the increase in wear resistance.
  • carbon content is excessive, too much carbides are formed, making the alloy brittle.
  • C is dissolved in the matrix to show the function of secondary hardening by tempering.
  • the toughness of the matrix is decreased.
  • the C content is 1.0-3.5 weight %.
  • the preferred C content is 1.5-3.0 weight %.
  • Si has a function of deoxidation, hardening of the alloy matrix, increasing oxidation resistance and corrosion resistance, and improving the atomizability of the alloy. To achieve these effects, the amount of Si is 0.2-1 weight %.
  • Mn is contained in an amount of 0,2-1 weight %, because it has a function of deoxidation and increasing the hardenability of the alloy.
  • the Cr not only contributes to the improvement of wear resistance by forming carbides with C but also enhances the hardenability of the alloy by dissolving into the matrix, and increasing the secondary hardening by tempering. However, when Cr is in an excess amount, the toughness of the matrix is lowered. Accordingly, the Cr content is 10 weight % or less. The preferred Cr content is 3-6 weight %.
  • W and Mo not only increase wear resistance by combining with C to form M 6 C-type carbides, but also are dissolved in the matrix, thereby increasing the hardness of the matrix when heat-treated. However, when they are in excess amounts, the toughness of the alloy decreases, and the material becomes expensive. Accordingly, W is 3-15 weight %, and Mo is 2-10 weight %. The preferred W content is 3-10 weight %, and the preferred Mo content is 4-10 weight %.
  • V is combined with C like W and Mo. It forms MC-type carbides which have a hardness Hv of 2500-3000, extremely larger than the hardness Hv of 1500-1800 of the M 6 C-type carbides. Accordingly, V is an element contributing to the improvement of wear resistance.
  • V content is lower than 1 weight %, its effect is too small.
  • the V content exceeds 15 weight %, the atomizability and workability of the alloy become poor. Accordingly, the V content is 1-15 weight %.
  • the preferred V content is 4-15 weight %.
  • Co is an element effective for providing the alloy with heat resistance, it may be added to the alloy powder. However, when it is in an excess amount, it lowers the toughness of the alloy. Accordingly, Co is preferably 3-15 weight %. The more preferred Co content is 5-10 weight %.
  • an alloy having the above composition is melted and formed into powder by a gas atomization method, etc.
  • the alloy powder obtained by such a method desirably has an average particle size of 30-300 ⁇ m.
  • the shell portion of the compound roll according to the present invention has a martensite or bainite matrix. Because of this matrix structure, the shell portion shows excellent mechanical strength.
  • the core portion of the compound roll may be made of any iron-base alloy materials such as cast iron, cast steel, forged steel, etc.
  • the alloy powder "P" obtained by atomization, etc. is charged into a metal capsule 2 disposed around a roll core portion 1.
  • the metal capsule 2 is evacuated through a vent 3 provided in an upper portion thereof and sealed, to keep the inside of the metal capsule 2 in a vacuum state. It is then subjected to a HIP treatment.
  • the metal capsule 2 may be made of steel or stainless steel plate having a thickness of about 3-10 mm.
  • the HIP treatment is usually conducted at a temperature equal to or higher than the temperature from which the alloy powder starts to be melted (hereinafter referred to as "melting-start temperature"). Specifically, the HIP treatment is conducted at a temperature of 1100-1300°C and a pressure of 9.81 - 14.715 ⁇ 10 3 N/cm 2 (1000-1500 atm) in an inert gas atmosphere such as argon, etc. for 1-8 hours, preferably 2-5 hours.
  • the most important feature of the present invention is that by conducting the HIP treatment at a temperature not lower than the melting-start temperature of the alloy powder, the sizes and distribution of carbides in the alloy matrix of the shell portion of the compound roll are controlled, thereby improving the wear resistance of the compound roll.
  • Figs. 1 and 9 which are photomicrographs showing the metal structures of Example 1 and Comparative Example 1, the sizes and distribution of carbides in the alloy matrix vary remarkably depending on the HIP treatment temperature even for the same alloy composition.
  • Fig. 9 which is a photomicrograph of the metal structure of Comparative Example 1, appears to indicate that fine carbide particles uniformly distributed in the alloy matrix are better than those having larger sizes.
  • the compound roll whose shell portion has such a metal structure shows poor wear resistance when the compound roll is used for rolling.
  • Fig. 1 verifies that the larger the sizes of the carbide particles in the matrix the higher wear resistance can be obtained.
  • the carbide particles contributing to improving the wear resistance of the compound roll have particle sizes of 3 ⁇ m or more, as shown in Fig. 1.
  • the carbide particles distributed in the alloy matrix have particle sizes less than 3 ⁇ m as shown in Fig. 9, it is considered that by the wearing mechanism shown in Fig. 3(b) the carbide particles do not substantially contribute to the improvement of the wear resistance of the compound roll.
  • the overall metal structure of the roll is deformed because the carbide particles 11 in the matrix 10 have small particle sizes. Accordingly, wearing of the roll takes place easily.
  • the carbide particles having particle sizes of 3 ⁇ m or more Even though there are carbide particles having particle sizes of 3 ⁇ m or more, the improvement of the wear resistance cannot be expected as long as the amount of the carbide particles is too small. Accordingly, the carbide particles having particle sizes within the range of 3 ⁇ m to 50 ⁇ m should occupy 15 % or more of the matrix by an area ratio.
  • the preferred area ratio of the carbide particles in the alloy matrix is 20-40 %.
  • the percentage of the number of the carbide particles having particle sizes of 3 ⁇ m or more to the number of the carbide particles having particle sizes of 0.5 ⁇ m or more should be 10 % or more. When the above percentage is less than 10 %, the wear resistance of the shell portion is deteriorated.
  • the preferred percentage of the number of the carbide particles having particle sizes of 3 ⁇ m or more to the number of the carbide particles having particle sizes of 0.5 ⁇ m or more is 10-40 %.
  • the compound roll having the metal structure meeting the above requirements shows improved wear resistance due to the mechanism shown in Fig. 3 (a). Specifically, even when the wearing particle 9 is brought into contact with the roll surface, the particle 9 is sustained by the large carbide particles 11, preventing the particle 9 from damaging the overall metal structure. By this mechanism, the roll is well protected from wearing.
  • the metal capsule 2 is removed by a lath. It is then subjected to a heat treatment in the pattern such as shown in Fig. 4. The desired compound roll is obtained after finish working.
  • Alloy powder having a composition shown in Table 1 was charged into a cylindrical metal capsule 2 disposed around a roll core portion 1 as shown in Fig. 2.
  • the metal capsule 2 was evacuated through a vent 3 in an upper portion thereof while heating the overall metal capsule 2 at about 500°C, and the vent 3 was sealed to keep the inside of the metal capsule 2 at about 1.333 ⁇ 10 -3 hPa (1 x 10 -3 torr).
  • this metal capsule 2 was placed in an argon gas atmosphere and subjected to a HIP treatment at a temperature of 1250 °C and at a pressure of 9.81 ⁇ 10 3 N/cm 2 (1000 atm) for 2 hours.
  • the temperature at which the alloy powder started to melt was 1195 °C.
  • Table 1 Chemical Components of Alloy Powder (weight %) C Si Mn Cr Mo W V Co Fe 2.5 0.4 0.4 4.0 5.3 8.8 6.9 8.4 Bal.
  • the outside metal capsule 2 was removed by lathing, and the resulting sample was subject to a heat treatment in the pattern shown in Fig. 4. Thereafter, the compound roll was subjected to finish work to provide a hollow compound roll consisting of a shell portion 4 made of a sintered alloy having an outer diameter of 350 mm and a thickness of 20 mm and a roll core portion 5 having an inner diameter of 250 mm and a length of 400 mm as shown in Fig. 5.
  • This compound roll had a shell portion 4 having a metal structure shown in Fig. 1.
  • Example 1 For comparison, a HIP treatment was conducted on the same compound roll as in Example 1 at a temperature of 1170 °C, lower than the above melting-start temperature of 1195°C, for the same period of time, and the same working as above was then conducted to provide a compound roll of Comparative Example 1.
  • the metal structure of the shell portion of the compound roll of Comparative Example 1 is shown in Fig. 9.
  • the compound rolls produced by the above method were subjected to an abrasive wear test method.
  • a test piece of 10 mm x 10 mm x 15 mm was machined from the shell portion of each compound roll, and subjected to a tempering treatment so that the test pieces 8 had various levels of hardness.
  • an emery paper 7 was attached to a test table 6, and the test table 6 was rotated.
  • Each test piece 8 was pushed onto the emery paper 7 under pressure of 598.6 N/mm 2 (60 kg mm 2 ) for 3 minutes to conduct the wear test.
  • the weight of the test piece was measured to evaluate a weight loss by wearing.
  • the results are shown in Fig. 7.
  • the straight line A denotes Example 1 and the straight line B denotes Comparative Example 1.
  • the weight loss of the compound roll of the present invention is about one-third that of the compound roll of Comparative Example 1 on the same hardness level. This means that the compound roll of the present invention (Example 1) is about three times as wear-resistant as the compound roll of Comparative Example 1.
  • Each compound roll consisted of a shell portion 4 made of a sintered alloy having the same composition as in Example 1 and having an outer diameter of 400 mm and a thickness of 30 mm, and a roll core portion 5 having an inner diameter of 280 mm and a length of 500 mm.
  • Each compound roll was formed with four round calibers each having a semi-circular cross section having a radius of 11 mm.
  • each compound roll was used as a finish roll for rolling a steel rod.
  • 690 tons of steel per each caliber was rolled by the compound roll of Example 2, while only 210 tons of steel per each caliber was rolled by the compound roll of Comparative Example 2.
  • the compound roll of the present invention is more than three times as wear-resistant as the compound roll of Comparative Example 2 which was subjected to a HIP treatment at a temperature lower than the melting-start temperature of the alloy powder for the shell portion.
  • the shell portion of the compound roll of the present invention is prepared by a HIP treatment at a temperature equal to or higher than the melting-start temperature of the alloy powder, the shell portion has carbide particles having large particle sizes. Therefore, the wear resistance of the compound roll of the present invention is as high as three times or more that of the conventional compound roll.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Composite Materials (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)

Claims (2)

  1. Cylindre composite résistant à l'usure ayant une partie formant enveloppe produite par frittage d'un poudre d'alliage comprenant 1,0 à 3,5 % en poids de C, 0,2 à 1 % en poids de Si, 0,2 à 1 % en poids de Mn, 10 % en poids ou moins de Cr, 3 à 15 % en poids de W, 2 à 10 % en poids de Mo, 1 à 15 % en poids de V, facultativement 3 à 15 % en poids de Co, et du Fe en reliquat et de impuretés inévitables, ladite partie formant enveloppe contenant des particules de carbure ayant des tailles de particule comprises dans la plage de 3 à 50 µm dans une matrice de martensite ou de bainite, et un rapport surfacique desdites particules de carbure dans ladite matrice de la partie formant enveloppe frittée étant de 15 % ou plus, dans lequel
    parmi lesdites particules de carbure ayant des tailles de particule de 0,5 µm ou plus, le nombre de particules de carbure ayant des tailles de particule de 3 µm ou plus est de 10 % ou plus.
  2. Cylindre composite selon la revendication 1, dans lequel ledit nombre de particules de carbure ayant des tailles de particule de 3 µm ou plus est de 10 40 %.
EP19920106860 1991-04-22 1992-04-22 Cylindre composite résistant à l'usure Expired - Lifetime EP0510598B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP9028091 1991-04-22
JP90280/91 1991-04-22

Publications (3)

Publication Number Publication Date
EP0510598A2 EP0510598A2 (fr) 1992-10-28
EP0510598A3 EP0510598A3 (en) 1993-07-14
EP0510598B1 true EP0510598B1 (fr) 1996-07-10

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ID=13994109

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19920106860 Expired - Lifetime EP0510598B1 (fr) 1991-04-22 1992-04-22 Cylindre composite résistant à l'usure

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EP (1) EP0510598B1 (fr)
DE (1) DE69212054T2 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06182409A (ja) * 1992-12-21 1994-07-05 Hitachi Metals Ltd 複合スリーブロール及びその製造方法
FR2833195B1 (fr) * 2001-12-07 2004-01-30 Giat Ind Sa Procede de mise en place d'un revetement de protection sur la paroi interne d'un tube, tube et notamment tube d'arme realise suivant ce procede
GB2492425B (en) * 2011-10-10 2013-05-15 Messier Dowty Ltd A method of forming a composite metal item
CN112547224B (zh) * 2020-11-27 2022-10-11 湖北秦鸿新材料股份有限公司 一种耐磨磨辊

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63195250A (ja) * 1987-02-10 1988-08-12 Daido Steel Co Ltd 圧延機用ロ−ル
JPH01252704A (ja) * 1988-03-31 1989-10-09 Kubota Ltd 複合部材およびその製造方法
US5053284A (en) * 1989-02-02 1991-10-01 Hitachi Metals, Ltd. Wear-resistant compound roll
JPH02270944A (ja) * 1989-04-13 1990-11-06 Hitachi Metals Ltd 耐摩耗，耐肌荒性ロール材及びその製造方法

Also Published As

Publication number Publication date
EP0510598A2 (fr) 1992-10-28
DE69212054T2 (de) 1996-11-07
EP0510598A3 (en) 1993-07-14
DE69212054D1 (de) 1996-08-14

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