EP0429796B1 - Heat-resistant materials - Google Patents

Heat-resistant materials Download PDF

Info

Publication number
EP0429796B1
EP0429796B1 EP90118741A EP90118741A EP0429796B1 EP 0429796 B1 EP0429796 B1 EP 0429796B1 EP 90118741 A EP90118741 A EP 90118741A EP 90118741 A EP90118741 A EP 90118741A EP 0429796 B1 EP0429796 B1 EP 0429796B1
Authority
EP
European Patent Office
Prior art keywords
alloy
heat
skid
temperature
resistant
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
EP90118741A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP0429796A1 (en
Inventor
Hideo Fujita
Jun Funakoshi
Takahiro Kaba
Akira Shinosaki
Hiroyuki Araragi
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.)
Kubota Corp
Original Assignee
Kubota Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=17880601&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0429796(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Kubota Corp filed Critical Kubota Corp
Publication of EP0429796A1 publication Critical patent/EP0429796A1/en
Application granted granted Critical
Publication of EP0429796B1 publication Critical patent/EP0429796B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/06—Alloys based on chromium

Definitions

  • the present invention relates to the use of heat-resistant materials as a skid button in heating furnaces, especially in heating furnaces of the walking beam type.
  • Heating furnaces of the walking beam type are used in the hot rolling process for heating steel materials such as steel pieces or slabs. These furnaces are equipped with skid beams in a plurality of rows for supporting and transporting steel pieces, slabs or like materials to be heated. These skid beams include movable beams and fixed beams. The movable beams periodically repeat an upward and downward movement and a horizontal reciprocating movement, whereby the material to be heated is transported while being transferred to the movable beam and the fixed beam alternately.
  • FIG. 1 shows a skid beam 1 which comprises a hollow skid pipe 10 provided on the top of its periphery with a plurality of skid buttons 12 arranged axially thereof at a specified spacing.
  • a refractory lining 5 covers the outer peripheral surface of the skid pipe 10 and the base to upper portion of each skid button 12 for use in the interior of the heating furnace.
  • the skid button 12 is a block in the form of a truncated cone, truncated pyramid or the like to support on the top thereof the material 3 to be heated.
  • Materials heretofore used for skid buttons are heat-resistant alloy steels such as high Ni high Cr alloy steels and high Co alloy steels (e.g., 50 Co-20 Ni-Fe steel).
  • Cooling water is forcibly passed through the skid pipe to diminish the thermal influence of the high-temperature oxidizing internal atmosphere of the furnace on the skid button and to prevent the rise in the temperature of the skid button. This assures the skid button of strength capable of withstanding the load of the material to be heated and prevents the surface of the skid button from oxidation damage.
  • the skid button is subject, for example, to deformation or oxidation damage.
  • the cooling action if excessive, entails the problem that the material to be heated and supported on the top of the skid button is locally cooled by contact with the skid button, which produces a so-called skid mark and permits uneven heating of the material.
  • skid buttons of conventional heat-resistant alloy have the problem of failing to withstand high operating temperatures and undergoing deformation due to the load of the material to be heated or oxidation damage or the like.
  • sintered ceramic bodies as skid buttons, ceramis are brittle materials, are therefore liable to crack or chip, and are not usable with good stability.
  • FR-A-2 137 793 discloses a heat-resistant alloy comprising at least 64 % of Cr, the balance substantially Fe and containing at least 5 % of Fe for ingot molds.
  • US-A-3 017 265 relates to an oxidation-resistant iron-chromium alloy comprising 20-95 % by weight of chromium, e.g. for applications In air.
  • US-A-2 780 545 discloses a forgeable high-temperature alloy comprising 60-80 % chromium for use in high-strength, high-temperature applications as required for turbine buckets In turbojet aircraft engines.
  • US-A-1 357 550 relates to an inexpensive, chemically-resistant alloy containing 40-60 % of chromium for the construction of tanks, valves, pipes, fittings, evaporation pans. stirrers and the like.
  • DE-A-1 608 116 describes a chromium-based alloy for the manufacture of electrodes for spark plugs.
  • US-A-4 442 067 relates to a chromium-based alloy for semi-conductor holder in an electron beam writing apparatus.
  • the present invention has been accomplished in view of the above problems.
  • skid button capable of exhibiting excellent high-temperature strength, in particular a small compressive deformation at high temperatures, and high resistance to oxidation for operation at high temperatures, for example in excess of 1300°C even if the cooling action of the skid pipe is not enhanced greatly.
  • the present invention relates to the use of a heat-resistant alloy comprising, in % by weight, at least 60% of Cr, optionally at least one or two elements selected from the group consisting of up to 10% of W, up to 10% of Mo, up to 10% of Nb, up to 10% of Ta, up to 10% of Hf, up to 10% of Co, up to 10% of Ni, up to 10% of Ti, up to 10% of Al, up to 10% of V, up to 10% of Mn and up to 10% of a rare-earth element in a combined amount of up to 35%, optionally up to 0.8 % of C and up to 5 % of Si, the balance being Fe plus incidental impurities, the alloy containing at least 5% of Fe and being at least 50 »m in the mean grain size of the alloy structure and at least 1600°C in melting point, as a skid button in heating furnaces.
  • a heat-resistant alloy comprising, in % by weight, at least 60% of Cr, optionally at least one or two elements selected from the group consisting of up to 10%
  • the present invention relates to the use of heat-resistant material having a composite structure wherein a dispersed ceramic phase is present in a metal matrix, the ceramic phase being present in a maximum amount of 40% by volume, the metal matrix comprising, in % by weight, at least 60% of Cr, optionally at least one or two elements selected from the group consisting of up to 10% of W, up to 10% of Mo, up to 10% of Nb, up to 10% of Ta, up to 10% of Hf, up to 10% of Co, up to 10% of Ni, up to 10% of Ti, up to 10% of Al, up to 10% of V, up to 10% of Mn and up to 10% of a rare-earth element in a combined amount of up to 35%, optionally up to 0.8 % of C and up to 5 % of Si, the balance being Fe, plus incidental impurities, the Fe being contained therein at least 5%, the metal matrix having a mean grain size of at least 50 »m and having a melting point of at least 1600°C, as a skid button in heating furnace
  • heat-resistant material used in the invention which is a heat-resistant alloy.
  • the heat-resistant alloy used in the present invention contains at least 60% of Cr.
  • the Cr content should be at least 60% to ensure a melting point of at least 1600° C and to obtain stable resistance to oxidation for use at high temperatures in excess of 1300° C.
  • the melting point of at least 1600° C is a prerequisite for giving excellent high-temperature strength.
  • the heat-resistant alloy used in the invention contains at least 5% of Fe.
  • the Fe content of at least 5% renders the alloy composition amenable to sintering and permits use of moderate sintering conditions when the alloy composition is to be sintered into an alloy while serving to moderate the thermal conditions for melting and casting operations when the composition is to be cast into an alloy. These effects are not available if the content is less than 5%.
  • the heat-resistant alloy used in the invention has a Cr-Fe composition comprising at least 60% of Cr, and the balance substantially Fe (which, however, should be present in an amount of at least 5%).
  • the alloy may further comprise one or at least two elements selected from the group consisting of up to 10% of W, up to 10% of Mo, up to 10% of Nb, up to 10% of Ta, up to 10% of Hf, up to 10% of Co, up to 10% of Ni, up to 10% of Ti, up to 10% of Al, up to 10% of V, up to 10% of Mn and up to 10% of a rare-earth element, in a combined amount of up to 35%, preferably up to 30%.
  • intermetallic compounds such as Cr2Nb, Cr2Zr, Cr2Ta and Cr2Ti
  • Cr2Nb, Cr2Zr, Cr2Ta and Cr2Ti then formed serve to strengthen the alloy more effectively by particle or fiber dispersion to give still improved alloy strength.
  • Al or rare-earth elements are expected to produce further improved resistance to oxidation in addition to an alloy strengthening effect.
  • the presence of excessive amounts of the above elements is likely to lower the melting point of the alloy below 1600° C and to impair the workability thereof, so that the upper limit of the combined amount should be 35%, preferably 30%.
  • the heat-resistant alloy is allowed to contain P, S and other impurities insofar as such impurities are inevitably incorporated into the alloy by usual alloy preparation techniques. Further up to 0.8% of C and up to 5% of Si are allowed to be present in the alloy.
  • heat-resistant material used in the present invention up to about 40% by volume of a ceramic can be present as a dispersed phase in the above heat-resistant alloy when so required.
  • Ceramics which can be present as dispersed in the alloy are oxides such as Cr2O3, Al2O3, SiO2, Y2O3, LaO and Sc2O3, nitrides such as Si3N4, TiN, BN and AlN, carbides such as B4C, Cr3C2, WC and SiC, silicides such as Mo2Si and Cr2Si, and borides such as CrB2 and TiB2.
  • oxides such as Cr2O3, Al2O3, SiO2, Y2O3, LaO and Sc2O3, nitrides such as Si3N4, TiN, BN and AlN, carbides such as B4C, Cr3C2, WC and SiC, silicides such as Mo2Si and Cr2Si, and borides such as CrB2 and TiB2.
  • oxides such as Cr2O3, Al2O3, SiO2, Y2O3, LaO and Sc2O3, nitrides such as Si3N4, TiN, BN and AlN, carb
  • the heat-resistant alloy or the heat-resistant material used in the present invention must be not only at least 1600° C in melting point but also at least 50 »m in the mean grain size of the alloy structure.
  • the crystal grains must be at least 50 »m in means size to give sufficient strength, especially satisfactory resistance to compressive deformation, in atmospheres having a high temperature in excess of 1300° C.
  • the heat-resistant alloy or material used in the present invention can be prepared by sintering, melt casting or other process, the crystal structure must be at least 50 »m in mean size regardless of the process resorted to.
  • the hot isostatic press sintering process in view of the homogeneity and compactness of the sintered alloy obtained.
  • This process can be practiced, for example, by heating the starting composition at a temperature of about 1000 to about 1500° C under a pressure of about 98 (1000) to about 196 MPa (2000 kgf/cm2) for about 2 to about 5 hours.
  • the grain size of the sintered alloy is dependent on the particle size of the powdery starting composition. We have found that when the starting composition is at least about 200 »m in mean particle size, the sintered alloy can be given a mean grain size of at least 50 »m.
  • the ceramic When a ceramic is to be made present in the alloy as a dispersed phase, the ceramic is used conjointly with the powdery starting alloy composition.
  • the ceramic can be of any desired size.
  • Useful particulate ceramics are, for example, about 0.1 to about 10 »m in particle size.
  • Examples of fibrous ceramics usable are about 1 to about 1000 »m in fiber length and about 10 to about 50 in aspect ratio.
  • the present alloy is to be prepared by casting, for example, a high-frequency melting furnace is usable.
  • the ceramic can be incorporated into the alloy as a dispersed phase by adding the ceramic as finely divided to the alloy in a molten state before the melt is poured into a mold or to the molten alloy as placed in the mold, and solidifying the mixture with the solid uniformly mixed with the melt.
  • the grain size of the alloy to be cast is adjustable with ease by controlling the solidification velocity of the mixture within the mold.
  • a sufficiently coarse crystal grain structure can be obtained by decreasing the solidification velocity with use of a sand mold, refractory mold or the like.
  • the heat-resistant alloy or material obtained by sintering or casting can be heat-treated for the adjustment of the grain size.
  • the mean grain size was determined by the following method. Five areas as desired were selected from the microstructure of the specimen, and photomicrographs (x50) was taken at each of the selected areas. Two vertical lines and two horizontal lines were drawn over each of the field of views, and the number of crystal grains were counted up. The total length of the lines was divided by the number of crystal grains to obtain a value as a mean of grain sizes. The average of the mean values for the five view fields was calculated as the mean grain size.
  • FIG. 9 shows a 12-second loading cycle comprising 4 seconds for the application of the compression load of 4.9 MPa (0.5 kgf/mm2), 4 seconds for allowing the test piece to stand free of the load, 2 seconds as a loading transition period and 2 seconds as an unloading transition period. This cycle was repeated 10000 times.
  • D (%) (Lo - L)/Lo x 100 where Lo is the length of the test piece before testing, and L is the length thereof after testing.
  • a solid cylindrical test piece (8 mm in diameter and 40 mm in length) was cut out from each specimen and held in a heating furnace (with air as atmosphere) at 1350° C for 100 hours. The test piece was then withdrawn from the furnace, scales were removed from the surface of the test piece with an alkali solution and an acid solution, and the oxidation loss (g/m2hr) was determined from the resulting change in the weight of the test piece.
  • Table 2 shows the results of the high-temperature compressive deformation test and the high-temperature oxidation test.
  • Table 2 Specimen No. Amount of compressive deformation, D (%) Oxidation loss (g/m2hr) 1 0.5 4.2 2 1.25 4.1 3 0.38 3.8 4 3.0 3.9 5 0.25 3.9 6 0.40 3.5 7 0.35 5.5 8 0.45 3.2 9 0.30 5.0 10 4.3 67.0 11 3.5 4.5
  • specimens No. 1 to No. 3 and No. 5 to No. 9 are examples of heat-resistant materials used in the invention.
  • Specimens No. 4 and No. 11 are comparative examples; with the former, the mean grain size is outside the range of the invention, and with the latter, the Cr content is outside the range of the invention.
  • Specimen No. 10 is Co-Ni-Cr alloy heretofore used for skid buttons.
  • Specimen No. 4 is great in compressive deformation at a high temperature presumably because it is small in mean grain size.
  • Specimen No. 11 is also great in compressive deformation at a high temperature. This appears attributable to a low Cr content and low melting point.
  • Specimen No. 10 is very low in melting point, great in compressive deformation and inferior in oxidation resistance.
  • heat-resistant alloys or materials used in the invention are very excellent in high-temperature strength and oxidation resistance.
  • FIG. 3 shows the relationship between the number of repetitions of compression load application and the variation in the amount of compressive deformation as determined by a high-temperature compression test.
  • FIG. 4 shows the relationship between the heating temperature and the oxidation loss as established by a high-temperature oxidation test. The specimens were tested for 100 hours at each of varying temperatures.
  • FIGS. 5 to 7 show the relationship between crystal grains and microstructure.
  • the photomicrographs (at a magnification of X50) of specimen No. 2 (50 »m in mean grain size), specimen No. 5 (200 »m in mean grain size) and specimen No. 4 (15 »m in mean grain size) are shown in FIGS. 5, 6 and 7, respectively.
  • Skid buttons were prepared from the heat-resistant alloy or material used in the present invention and attached to a skid pipe by support members as seen in FIG. 2.
  • the illustrated embodiment is adapted to prevent scales separating off the surface of the material heated from wedging into the support members and to preclude the skid buttons from chipping, cracking and like faults by giving consideration to the difference in the amount of thermal expansion due to the difference in material between the skid buttons and the support members.
  • the skid button 12 shown in FIG. 2 is in the form of a truncated cone and has a flange 14 at its bottom.
  • the skid button 12 can be in the form of a solid cylinder, truncated pyramid or the like.
  • a support member 4 comprises a seat portion 44 formed with an annular cavity 42 for the flange 14 of the skid button 12 to fit in loosely, and a ring member 46 having an inside diameter slightly larger than the outside diameter of the shank of the skid button 12.
  • the bottom of the seat portion 44 is secured to a skid pipe 10 as by a weld W.
  • the ring member 46 is secured to the seat portion 44 as by a weld W, whereby the skid button 12 is held to the support member 4.
  • the outer periphery of the skid pipe 10 and the base to upper portion of the support member 4 are covered with a refractory layer 5 and are thereby protected from the high-temperature oxidizing atmosphere within the furnace.
  • the refractory of the layer 5 fills the clearance C between the skid button 12 and the ring member 46, so that the scales separating off a material 3 heated and placed on the skid button 12 are prevented from falling into the clearance C. Consequently, the ring member 46 is prevented from deformation due to the ingress of scales.
  • the skid button 12 is about 100 to about 200 mm in height.
  • the height of the skid button 12 projecting upward beyond the ring member 46 of the support member 4 is preferably about 50 to about 100 mm.
  • the heat-resistant alloy or heat-resistant material used in the present invention is excellent in high-temperature strength and in resistance to oxidation, and these excellent characteristics are in no way available with high Co alloy steels and like materials heretofore used. Accordingly, the skid buttons prepared from the heat-resistant alloy or material in accordance with the invention exhibit sufficient durability even under such high-temperature operating conditions as employed recently, diminishing the maintenance effort and thereby contributing a great deal to improvements in operation efficiency.
  • the excellent high-temperature characteristics of the present material serve to moderate the cooling conditions for the cooling water to be passed through the skid pipe. This reduces the likelihood of occurrence of skid marks on the material to be heated and achieves uniform heating for the production of materials of improved quality.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatments In General, Especially Conveying And Cooling (AREA)
  • Powder Metallurgy (AREA)
EP90118741A 1989-11-17 1990-09-28 Heat-resistant materials Expired - Lifetime EP0429796B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP1300091A JP2607157B2 (ja) 1989-11-17 1989-11-17 加熱炉内の被加熱鋼材支持部材用耐熱合金
JP300091/89 1989-11-17

Publications (2)

Publication Number Publication Date
EP0429796A1 EP0429796A1 (en) 1991-06-05
EP0429796B1 true EP0429796B1 (en) 1995-12-13

Family

ID=17880601

Family Applications (1)

Application Number Title Priority Date Filing Date
EP90118741A Expired - Lifetime EP0429796B1 (en) 1989-11-17 1990-09-28 Heat-resistant materials

Country Status (5)

Country Link
EP (1) EP0429796B1 (ko)
JP (1) JP2607157B2 (ko)
KR (1) KR0134182B1 (ko)
AU (1) AU632166B2 (ko)
DE (1) DE69024179T2 (ko)

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2571640Y2 (ja) * 1991-09-20 1998-05-18 株式会社クボタ 加熱炉用スキツドボタン
JP2571641Y2 (ja) * 1991-09-20 1998-05-18 株式会社クボタ 加熱炉用スキツドボタン
JP2702631B2 (ja) * 1991-12-12 1998-01-21 株式会社クボタ 炉床開口カバー支持用部材
JPH05271840A (ja) * 1992-03-27 1993-10-19 Kobe Steel Ltd 超高温耐熱部材用Ｃｒ基合金
JPH062066A (ja) * 1992-06-15 1994-01-11 Kubota Corp 加熱炉内支持面部材用耐熱合金
JPH062065A (ja) * 1992-06-15 1994-01-11 Kubota Corp 加熱炉内支持面部材用耐熱合金
JP3480698B2 (ja) 1999-05-27 2003-12-22 兼次 安彦 高温における強度−延性バランスに優れるＣｒ基合金
KR100396368B1 (ko) * 2001-04-17 2003-09-03 부공산업 주식회사 고온강도와 고온내산화성이 우수한 초내열합금
JP4061407B2 (ja) * 2003-10-10 2008-03-19 独立行政法人物質・材料研究機構 耐熱部品用クロム合金
KR101030222B1 (ko) * 2010-11-18 2011-04-22 부공산업 주식회사 내식성이 우수한 스키드레일용 초내열합금
CN108546860A (zh) * 2018-04-27 2018-09-18 苏州弗士曼精密机械有限公司 一种高温抗氧化性不锈钢金属
KR102365404B1 (ko) * 2019-12-04 2022-02-21 (주)영신특수강 로부품용 고크롬 내열합금 및 그 제조방법
CN113621842A (zh) * 2021-08-05 2021-11-09 烟台百思特炉管厂 一种轧钢加热炉加热段垫块材料的生产工艺
CN115323234B (zh) * 2022-08-09 2023-08-01 东睦新材料集团股份有限公司 一种无磁低膨胀铬基合金材料的制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1357550A (en) * 1919-08-25 1920-11-02 Frank A Fahrenward Chemical ware or technical apparatus and alloys for making same
US2780545A (en) * 1954-02-03 1957-02-05 Battelle Development Corp High-temperature alloy
US3017265A (en) * 1959-09-25 1962-01-16 Gen Electric Oxidation resistant iron-chromium alloy
DE1608116A1 (de) * 1967-12-14 1970-12-10 Schmid Geb Reiniger Dipl Ing S Legierungen auf Chrombasis fuer Elektroden,insbesondere Zuendkerzenelektroden
DE2221220C3 (de) * 1971-05-12 1974-01-17 Gebrueder Sulzer Ag, Winterthur (Schweiz) Verwendung einer Chrom-Basis-Legierung als Kokillenwerkstoff
US4011941A (en) * 1975-04-28 1977-03-15 Warner-Lambert Company Contact lens capsule
JPS524248A (en) * 1975-06-27 1977-01-13 Dainippon Toryo Co Ltd Liquid crystal glasses
JPS5248090A (en) * 1975-10-14 1977-04-16 Furukawa Electric Co Ltd:The Method of manufacturing a connector
JPS5930781B2 (ja) * 1976-08-31 1984-07-28 財団法人特殊無機材料研究所 シリコンカ−バイド繊維強化クロム基高強度耐熱耐食合金複合材料およびその製造方法
JPS58107632A (ja) * 1981-12-22 1983-06-27 Tohoku Tokushuko Kk 電子ビ−ム描画装置用材料

Also Published As

Publication number Publication date
JPH03162545A (ja) 1991-07-12
DE69024179D1 (de) 1996-01-25
AU632166B2 (en) 1992-12-17
EP0429796A1 (en) 1991-06-05
KR910009945A (ko) 1991-06-28
JP2607157B2 (ja) 1997-05-07
KR0134182B1 (ko) 1998-06-15
DE69024179T2 (de) 1996-08-01
AU6329690A (en) 1991-05-23

Similar Documents

Publication Publication Date Title
EP0429796B1 (en) Heat-resistant materials
EP0510495B1 (en) Oxide-dispersion-strengthened heat-resistant sintered alloy
EP1094125B2 (en) Maraging steel excellent in fatigue characteristics and method for producing the same
US3180012A (en) Cobalt alloys
US5608174A (en) Chromium-based alloy
EP0326371B1 (en) Skid rail
EP1314498B1 (en) Method for producing a composite material
JPS60200948A (ja) 加熱炉の支持部材用複合材料
US5288228A (en) Heat-resistant materials
EP0441574B1 (en) Skid member using Fe/Cr dispersion strengthened alloys
CA2215447C (en) Heat-resistant alloy steel for hearth metal members of steel material heating furnaces
JPH04301049A (ja) 加熱炉内被加熱鋼材支持面部材用耐熱合金
US5226980A (en) Skid rail alloy
JPS6310114B2 (ko)
EP0441573B1 (en) Heat-resistant alloy
JP2772305B2 (ja) ムライト／窒化硼素複合ブレークリング及びセラミック複合体を製造する方法
JPH04301047A (ja) 加熱炉内被加熱鋼材支持面部材用耐熱合金
Tiegs et al. Microstructure Development During Sintering of TiC-Ni~ 3Al Cermets
US6458733B1 (en) Reinforced refractory product
JPH0297614A (ja) 加熱炉内の鋼材搬送部材
JPS63391B2 (ko)
DAVIDSON Micromechanisms of fatigue crack growth and fracture toughness in metal matrix composites(Technical Report, 31 Oct. 1987- 31 Jul. 1988)
JPH062065A (ja) 加熱炉内支持面部材用耐熱合金
Piekarski Properties of Stabilised Ni-Cr Cast Steel Exposed to the Effect of Carburising Atmosphere and Thermal Fatigue
JPH02175679A (ja) 耐熱支持部材

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): BE DE FR GB IT NL

17P Request for examination filed

Effective date: 19911024

17Q First examination report despatched

Effective date: 19930917

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): BE DE FR GB IT NL

ITF It: translation for a ep patent filed

Owner name: JACOBACCI & PERANI S.P.A.

ET Fr: translation filed
REF Corresponds to:

Ref document number: 69024179

Country of ref document: DE

Date of ref document: 19960125

NLT2 Nl: modifications (of names), taken from the european patent patent bulletin

Owner name: KUBOTA CORPORATION

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

26N No opposition filed
REG Reference to a national code

Ref country code: GB

Ref legal event code: IF02

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20090915

Year of fee payment: 20

Ref country code: GB

Payment date: 20090923

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20090923

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 20090825

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20090917

Year of fee payment: 20

Ref country code: FR

Payment date: 20091012

Year of fee payment: 20

BE20 Be: patent expired

Owner name: *KUBOTA CORP.

Effective date: 20100928

REG Reference to a national code

Ref country code: NL

Ref legal event code: V4

Effective date: 20100928

REG Reference to a national code

Ref country code: GB

Ref legal event code: PE20

Expiry date: 20100927

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20100927

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20100928

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20100928