EP0144907A2 - Verfahren zur Herstellung von Gegenständen aus Gusseisen mit Kugelgraphit durch Umwandlung in der Bainitstufe - Google Patents

Verfahren zur Herstellung von Gegenständen aus Gusseisen mit Kugelgraphit durch Umwandlung in der Bainitstufe Download PDF

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Publication number
EP0144907A2
EP0144907A2 EP84114386A EP84114386A EP0144907A2 EP 0144907 A2 EP0144907 A2 EP 0144907A2 EP 84114386 A EP84114386 A EP 84114386A EP 84114386 A EP84114386 A EP 84114386A EP 0144907 A2 EP0144907 A2 EP 0144907A2
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Prior art keywords
cast iron
spheroidal graphite
temperature
cooling
graphite cast
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Withdrawn
Application number
EP84114386A
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English (en)
French (fr)
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EP0144907A3 (de
Inventor
Yoshio Jimbo
Mamoru Sayashi
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Nissan Motor Co Ltd
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Nissan Motor Co Ltd
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Publication of EP0144907A2 publication Critical patent/EP0144907A2/de
Publication of EP0144907A3 publication Critical patent/EP0144907A3/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/04—Cast-iron alloys containing spheroidal graphite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D5/00—Heat treatments of cast-iron

Definitions

  • This invention relates to a spheroidal graphite cast iron, and more particularly to a method of producing an austempered spheroidal graphite cast iron body and the product of the same.
  • austempered spheroidal graphite cast irons which can be called bainitic spheroidal graphite cast irons, have a remarkably better combination of tensile strength and elongation or toughness than conventional ferritic or pearlitic spheroidal graphite cast irons.
  • austempering of spheroidal graphite cast irons has found only limited applications to small-sized and thin-wall parts because it is not easy to accomplish ideal austempering or utilization of high bainite by heat treatment of ordinary spheroidal graphite cast irons.
  • the fundamental reason for the difficulty in austempering spheroidal graphite cast irons of the popular compositions is that the stability of supercooled austenite is insufficient. Therefore, it is required for accomplishment of' proper austempering that the cast iron be cooled from the austenizing temperature to the bainite transformation temperature at a sufficiently high rate of temperature reduction.
  • a method for producing an austempered spheroidal graphite cast iron body comprises the steps of (a) casting a spheroidal graphite composition, which consists of 3.0 to 4.0 wt% of C, 1.5 to 3.0 wt% of Si, 0.005 to 0.2 wt% of a spheroidizing agent, 0.3 to 0.8 wt% of Mn, 0.3 to 2.0 wt% of Cu, 0 to 0.1 wt% of Mo, 0 to 0.3 wt% of Ni and the balance of Fe and inevitable impurities, into a desirably shaped body, and (b) austempering the cast iron body by first keeping the cast iron body at a first temperature at which austenite is stabilized, cooling the cast iron body from the first temperature to a second temperature at which transformation of austenite into bainite takes place at such a cooling rate that the cooling is accomplished substantially without precipitation of pearlite, keeping the cast iron body at said second temperature to accomplish isothermal transformation of
  • the cooling rate mentioned at the step (b) is in the range from 10°C/sec to 0.64°C/sec, and it is also preferred to perform the cooling from the austenite stabilizing temperature to the bainite transformation temperature in a fluidized bed furnace.
  • An important feature of the present invention is the coexistence of 0.3-0.8 wt% of Mn and 0.3-2.0 wt% of Cu in the spheroidal graphite cast iron.
  • the above specified range of the cooling rate is preferred from the viewpoints of surely preventing precipitation of pearlite and minimizing the strains produced in the cast iron body by the austempering heat treatment.
  • the cooling can be accomplished by air cooling.
  • a salt bath or a metal bath it is possible to use a salt bath or a metal bath to realize a desired cooling rate even in the interior portions of the cast iron bodies.
  • a fluidized bed furnace is preferred to salt or metal baths firstly because the former does not involve the problems mentioned hereinbefore in respect of salt baths and also because the austempered products have better mechanical properties when the cooling is performed in a fluidized bed furnace.
  • a fluidized bed furnace it is possible to apply the present invention to very thick-wall parts such as automotive crankshafts or to accomplish austempering of thick-wall parts so as to fully utilize high bainite.
  • a suitable range of the austenite stabilizing temperature is from about 800°C to about 1000 0 C, and preferably from 850 to 950°C,
  • a suitable range of the bainite forming temperature is from about 200°C to about 400°C.
  • the present invention has made it practicable to use an inexpensive spheroidal graphite cast iron in place of expensive high molybdenum and/or high nickel spheroidal graphite cast irons for producing thick-wall machine parts that are high in both strength and toughness or machine parts that utilize high bainite.
  • This invention is applicable to a wide variety of structural machine parts such as gears, joints, cylinders, casings, drums, forks, crankshafts, rocker arms, cylinder rings and so forth.
  • composition of a spheroidal graphite cast iron must be as specified hereinbefore.
  • the effects of the respective alloying elements and the reasons for the limitations on the amounts of the respective elements are as follows. Throughout the following description, the amounts of the elements in the cast irons are given in percentages by weight.
  • Carbon is an alloying element indispensable to cast irons.
  • the content of C is limited to a maximum of 4.0% because the presence of more than 4.0% of C together with Si tends to cause crystallization of graphite as primary crystal, which is unfavorable for the strength and toughness of the cast iron. If the content of C is too low, the cast iron composition becomes inferior in castability. Therefore, the minimum content of C is set at 3.0%.
  • Silicon is an alloying element that plays an important role in accomplishing graphitization in the cast iron. If the content of Si is too low the cast iron composition is unsatisfactory in castability and also in the degree of graphitization. On the other hand, if the content of Si is too high the cast iron becomes insufficient in elongation and unfavorably brittle. In view of such tendencies, the content of Si in a spheroidal graphite cast iron according to the invention is limited within the range from 1.5 to 3.0%.
  • manganese is used as an alloying element that makes an important contribution to enhancement of the stability of supercooled austenite in the spheroidal graphite cast iron.
  • the minimum content of Mn is set at 0.3% because the expected effect is insufficient if the Mn content is less than 0.3%.
  • the content of Mn is limtted to a maximum of 0.8% because the addition of a larger amount of Mn is liable to cause lowering of the strength and toughness of the cast iron.
  • Copper has the effect of improving the susceptibility of the spheroidal graphite cast iron to heat treatment.
  • the minimum content of Cu is set at 0.3% because the expected effect is insufficient if the Cu content is less than 0.3%.
  • the presence of a relatively large amount of Cu offers a difficulty to the spheroidization of graphite, and the addition of an unnecessarily large amount of Cu results in lowering of the tensile strength and impact resistance of the spheroidal graphite cast iron. Therefore, the content of Cu is limited to a maximum of 2.0%.
  • a spheroidizing agent can freely be selected from well known spheroidizing elements such as Mg, Ca and Ce, though we prefer Mg to other spheroidizing elements.
  • a suitable range of the content of Mg or an alternative spheroidizing agent in a cast iron composition in this invention is from 0.005% to 0.2%.
  • molybdenum is an optional alloying element which is effective in enhancing the stability of supercooled austenite in the cast iron.
  • the content of Mo is limited to a maximum of 0.1% because the addition of a larger amount of Mo tends to result in lowering of the tensile strength and toughness of the cast iron and also because Mo is an expensive material.
  • nickel too is an optional alloying element effective in enhancing the stability of supercooled austenite in the cast iron.
  • the content of Ni is limited to a maximum of 0.3% because when the content of Ni is more than 0.3% there arises a tendency for Ni to suppress bainite transformation rather than pearlite transformation and, therefore, it takes a longer time to accomplish transformation into bainite with little degradation of the mechanical properties of the austempered cast iron, and also because Ni is an expensive material.
  • a spheroidal graphite cast iron according to the invention contains very small amounts of impurities besides the above described essential and optional alloying elements and Fe. Typical examples of such impurities are phosphorus and sulfur. It is desirable that the content of P is below 0.1% because a higher content of P is detrimental to the workability of the cast iron. Also it is desirable that the content of S is below 0.1% because a higher content of S is obstructive to the spheroidization of graphite.
  • the cast iron composition was cast and machined into test pieces of an annular shape as shown in Fig. 1.
  • Each test piece 10 was 8 mm in outer diameter, 6 mm in inner diameter and 2 mm in thickness and was formed with a cut 12 of which the width D was 2 mm. On every test piece 10 the width D of the cut 12 was measured to an accuracy of the order of 0.001 mm.
  • The'test pieces were individually subjected to an austempering heat treatment by using a transformation point measuring apparatus, which was capable of heating the test piece to a desired temperature in a vacuum atmosphere by means of a high frequency heating coil and then cooling the heated test piece at a variably prescribed rate by blowing nitrogen gas or hydrogen gas against the test piece.
  • a transformation point measuring apparatus which was capable of heating the test piece to a desired temperature in a vacuum atmosphere by means of a high frequency heating coil and then cooling the heated test piece at a variably prescribed rate by blowing nitrogen gas or hydrogen gas against the test piece.
  • Each test piece was first heated up to 900°C for stabilization of austenite and kept at this temperature for 2 hr. After that the test piece was cooled down to 300°C at a constant cooling rate which was selectively prescribed within the range from 0.5°C/sec to 30°C/sec, and kept at 300°C for 2 hr. After that the apparatus was disconnected from the power source to allow the test piece to cool down to room temperature.
  • the width D of the cut 12 of each test piece 10 was measured to an accuracy of the order of 0.001 mm to find a change in the cut width D produced by the heat treatment as the absolute value of the difference between the width D before heat treatment and the width D after heat treatment.
  • This dimensional change is attributed to a strain produced by the heat treatment and the expansion of the test piece by reason of a change in the cast iron structure by transformation.
  • Fig. 2 shows the result of this experiment.
  • the magnitudes of the change in the cut width D are relative values compared with the value of the dimensional change at the cooling rate of 0.8°C/sec, which was a very low cooling rate close to a critical rate below which the precipitation of pearlite is probable.
  • the strain produced by the heat treatment and represented by the dimensional change of the test piece was sufficiently small when the cooling rate was not higher than 10°C/sec. However, when the cooling rate was lower than 0.64°C/sec a considerable increase in the dimensional change was observed. This is not because of augmentation of the strain produced by the heat treatment, and this is attributed to the precipitation of some pearlite.
  • the cooling from an austenite stabilizing temperature to a bainite transformation temperature at a cooling rate in the range from 10°C/sec to 0.64°C/sec with a view to minimizing the strain attributed to the heat treatment.
  • An optimum cooling rate is variable within this range depending on the composition of the spheroidal graphite cast iron.
  • the spheroidal graphite cast iron composition described in Experiment 1 was cast and machined into test pieces of a cylindrical shape as shown in Fig. 3.
  • the length L and outer diameter D of the test piece 20 were varied so as to obtain four differently sized test pieces 20 as shown in Table 1.
  • Each test piece 20 was formed with a central bore 22 of a small diameter, and a Pt-Pt13%Rh thermocouple (not shown) was inserted into the hore 22 and spot-welded to the test piece at the bottom 24 of the bore 22.
  • Fig. 4 shows a fluidized bed furnace 30 used in this experiment.
  • the body of the furnace 30 was a cylindrical metal container 32 which was 610 mm in inner diameter and 600 mm in depth.
  • the container 32 was provided with a gas diffusion plate 34 of a porous or sintered metal plate, and the space above the gas diffusion plate 34 was filled with an alumina powder 36 which was employed as a heat transferring medium.
  • the alumina powder 36 consisted of particles that passed through 80-mesh screen. In general it is suitable to use alumina (or an alternative material) particles that pass through 60-mesh screen but do not pass through 100-mesh screen in a fluidized bed furnace for use in the present invention.
  • a gas feed pipe 38 is connected to the container 32 at the bottom section to blow an inactive gas such as nitrogen gas into the bed of the alumina powder 36 through the gas diffusion plate 34.
  • the furnace 30 has electric heaters 40 disposed circumferentially of the container 32.
  • the alumina powder 36 is heated by the heaters 40 and is forcibly fluidized by the action of the gas flowing upward through the diffusion plate 34 and, therefore, provides a uniformly heated fluidized bed.
  • the flow rate of the gas through the pipe 38 is suitably regulated according to the capacity of the furnace 30 and the specified heating temperature. In this experiment, nitrogen gas was supplied at a rate of 250 liters/min.
  • each test piece 20 was placed in a supporting basket 42 made of a stainless steel and first heated in a separate electric furance which was maintained at a constant temperature of 900°C.
  • the test pieces 20 was kept in the electric furnace for 4 hr after the interior temperature of the test piece 20 reached 900°C.
  • the basket 42 containing the heated test piece 20 was quickly transferred into the fluidized bed furnace 30 in which the heating medium 36 had already been heated to 300°C.
  • the basket 42 was kept in position such that the test piece 20 is located in a central region of the heating medium 36, and the temperature in the interior of each test piece 20 was continuously recorded to examine the rate of drop in the temperature.
  • the rate of cooling from 900°C to 300°C was as shown in Table 2.
  • the test pieces 20 of the types A and D were cooled in a salt bath. In this case, each sample was kept at 900°C for 4 hr and then put into a salt bath which was maintained at about 300°C. The cooling rates measured in this case are also shown in Table 2.
  • spheroidal graphite cast iron compositions according to the invention were produced by adding variable amounts of Mn, Cu, Mo and Ni to a fundamental composition which was an example of commonly used spheroidal graphite cast iron compositions.
  • the fundamental cast iron composition consisted of 3.6% of C, 2.6% of Si, 0.04% of Mg, 0.05% of Cr, 0.02% of P, 0.007% of S and the balance of Fe.
  • the content of Mn was varied within the range from 0.4 to 0.8% and the content of Cu within the range from 0.4 to 2.0%
  • the content of Mo was varied within the range from 0.00 to 0.10% and the content of Ni within the range from 0.00 to 0.29%.
  • Each of the spheroidal graphite cast iron compositions of Examples 1-6 was cast and machined into test pieces and then austempered by first heating at 900°C for 4 hr, then cooling to 250°C in a salt bath, thereafter keeping at 250°C for 2 hr and then quenching in water. On the thus treated test pieces, the tensile strength and Charpy impact value were measured by the standard methods. The results are shown in Table 3.
  • TTT time-temperature-transformation
  • Table 3 contains the values of the latent period t i of a pearlite nose which appeared in the TTT diagram. It can be said that as the value of t i is larger austenite is more stable and the transformation into pearlite is less probable.
  • Supplemental to this experiment the same measurement was made on separately prepared spheroidal graphite cast iron compositions. These compositions were prepared by adding 0.01% of Mo and 0.20% of Ni to the aforementioned fundamental composition and further adding Mn and/or Cu in various amounts as shown in Fig. 5.
  • the spheroidal graphite cast iron compositions of Examples 1-6 were modified by greatly increasing the contents of Mo and/or Ni and also by varying the contents of Mn and/or Cu, as shown in Table 3.
  • Reference 3 can be regarded as the spheroidal graphite cast iron shown in the Japanese specification No. 54-133420 mentioned hereinbefore.
  • the tests described in Examples 1-6 were made on the samples of References 1-7 too. The results are contained in Table 3.
  • the position of the bainite transformation line was also checked. It was confirmed that when the content of Ni was more than 0.3% the transformation into bainite required a longer time than in the other cases.
  • the latent period for bainite transformation at 250°C was measured to be about 800 see in the case of Example 6 (Ni 0.29%) and about 2000 sec in the case of Reference 5 (Ni 0.48%).
  • a spheroidal graphite cast iron composition consisting of 3.6% of C, 2.6% of Si, 0.04% of Mg, 0.6% of Mn, 1.5% of Cu, 0.05% of Mo, 0.20% of Ni, 0.05% of Cr, 0.02% of P, 0.007% of S and the balance of Fe was cast and machined into three kinds of test pieces of the shapes shown in Figs. 6, 7 and 8, respectively.
  • the test piece 50 of Fig. 6 was for a tensile test. This test piece 50 had a diameter of 7 mm in its cylindrical middle portion, and the gauge length was 40 mm.
  • the test piece 60 of Fig. 7 was for Charpy impact test. This test piece 60 was 10 x 10 mm square by 55 mm long and had a slit-like cut 62 which was 3 mm in depth.
  • the test piece 70 of Fig. 8 was for fatigue test by a rotary bending tester. This test piece 70 was 200 mm long and had a diameter of 16 mm in both end portions, which were each 70 mm long, and a reduced diameter of 8 mm in a cylindrical middle portion.
  • the three kinds of cast iron test pieces 50, 60, 70 were respectively divided into two groups in order to perform austempering of these test pieces by two different methods.
  • the test pieces of one group were kept immersed for 4 hr in a chloride salt bath which was maintained at 900°C, then immersed in a nitrate salt bath maintained at 300°C and kept in that state for 2 hr, and then quenched in water.
  • test pieces of the other group were first heated at 900 0 C for 4 hr in a nitrogen gas atmosphere in an electric furnace, then transferred into the fluidized bed furnace 30 of Fig. 4 in which the heating medium 36 was maintained at 300°C and kept therein for 5 min, then transferred into an electric furnace filled with nitrogen gas and maintained at 300 0 C and kept therein for 1 hr and 55 min, and thereafter quenched in water.
  • test pieces 50, 60, 70 austempered by either of these two methods were subjected to a tensile test, Charpy impact test or a rotary bending test as a fatigue test.
  • Table 4 shows the results of the tests.
  • the fatigue strength refers to the maximum stress the test piece 70 could endure for 10 6 times of bending stress cycles without breaking.
  • test results in Table 4 demonstrate that in the austempering heat treatment according to the invention, better results with respect to the mechanical properties of the treated castings can be obtained by using a fluidized bed furnace for the cooling to form bainite instead of a salt bath.

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
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EP84114386A 1983-12-05 1984-11-28 Verfahren zur Herstellung von Gegenständen aus Gusseisen mit Kugelgraphit durch Umwandlung in der Bainitstufe Withdrawn EP0144907A3 (de)

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JP228327/83 1983-12-05
JP58228327A JPS60121253A (ja) 1983-12-05 1983-12-05 球状黒鉛鋳鉄

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EP0144907A2 true EP0144907A2 (de) 1985-06-19
EP0144907A3 EP0144907A3 (de) 1986-11-05

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Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0203050A1 (de) * 1985-05-22 1986-11-26 Ab Volvo Verfahren zur Herstellung von einem zwischenstufengehärteten Kugelgraphit-Gusseisen
EP0262324A1 (de) * 1986-09-30 1988-04-06 Union Carbide Corporation Verfahren zum Schnellabschrecken im Wirbelbett
FR2712606A1 (fr) * 1993-11-19 1995-05-24 Tech Ind Fonderie Centre Procédé d'élaboration d'une charge de fonte à graphite sphéroïdal à caractéristiques mécaniques élevées.
EP0747154A1 (de) * 1995-06-07 1996-12-11 MANNESMANN Aktiengesellschaft Verfahren und Vorrichtung zur Herstellung von Sinterteilen
US5753055A (en) * 1996-11-05 1998-05-19 Standard Car Truck Company Process for austempering ductile iron
EP1029098A1 (de) * 1997-10-14 2000-08-23 Camcast Industries Pty. Ltd Eisenlegirung mit molybdän
FR2839727A1 (fr) * 2002-05-14 2003-11-21 Technologica Sarl Procede d'elaboration et de mise en forme de pieces en fonte a graphite spheroidal a caracteristiques mecaniques elevees
FR2866351A1 (fr) * 2004-02-12 2005-08-19 Technologica Sarl Procede de fabrication de pieces en fonte a graphite spheroidal de grande precision geometrique et dimensionnelle et a caracteristiques mecaniques ameliorees
WO2011042123A1 (de) * 2009-10-05 2011-04-14 Bayerische Motoren Werke Ag Gusseisen-gussteil und verfahren zu dessen herstellung
EP2471960A1 (de) * 2010-12-30 2012-07-04 Casa Maristas Azterlan Verfahren zur Herstellung einem Kugelgraphit-Gusseisenteil
US10337089B2 (en) 2014-07-25 2019-07-02 Ford Global Technologies, Llc Process for producing a component made of heat-treated cast iron
CN110561405A (zh) * 2018-06-05 2019-12-13 精工爱普生株式会社 机器人、齿轮装置以及齿轮装置的制造方法
CN112609054A (zh) * 2020-11-09 2021-04-06 广西玉柴机器股份有限公司 一种耐疲劳气缸盖的工艺方法
CN116574874A (zh) * 2023-04-15 2023-08-11 盐城震业机械股份有限公司 一种等温淬火球墨铸铁的制备方法

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JPH075959B2 (ja) * 1986-05-02 1995-01-25 日産自動車株式会社 耐摩耗性鋳鉄部材の製造方法
JPS63105920A (ja) * 1986-10-23 1988-05-11 Toyota Autom Loom Works Ltd 鋳鉄品の熱処理方法
JP2008280619A (ja) * 2008-08-08 2008-11-20 Oume Chuzo Kk 高強度球状黒鉛鋳鉄
CN103320680B (zh) * 2013-06-28 2015-10-14 常州钜苓铸造有限公司 一种球墨铸铁及其制备方法
CN103320674B (zh) * 2013-07-11 2015-10-21 朱瑞辉 一种带碳化物等温淬火球铁及其淬火工艺

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DE1012317B (de) * 1952-02-21 1957-07-18 Renault Herstellung von Tempergussstuecken hoher Zaehigkeit
GB840490A (en) * 1957-06-06 1960-07-06 Goetzewerke Improvements relating to the manufacture of piston rings
FR2192184A1 (de) * 1972-07-12 1974-02-08 Kymin Oy Kymmene Ab
EP0018445A1 (de) * 1978-12-13 1980-11-12 Horst Dr. Mühlberger Verfahren zur Herstellung von Gussstücken aus Gusseisen mit Kugelgraphit

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METAL SCIENCE AND HEAT TREATMENT, vol. 18, no. 5/6, May/June 1976, pages 503-506, Plenum Publishing Corp., New York, US; L.A. SOLNTSEV et al.: "Effect of heating temperature on microstructure and properties of magnesium cast iron" *

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0203050A1 (de) * 1985-05-22 1986-11-26 Ab Volvo Verfahren zur Herstellung von einem zwischenstufengehärteten Kugelgraphit-Gusseisen
EP0262324A1 (de) * 1986-09-30 1988-04-06 Union Carbide Corporation Verfahren zum Schnellabschrecken im Wirbelbett
FR2712606A1 (fr) * 1993-11-19 1995-05-24 Tech Ind Fonderie Centre Procédé d'élaboration d'une charge de fonte à graphite sphéroïdal à caractéristiques mécaniques élevées.
EP0747154A1 (de) * 1995-06-07 1996-12-11 MANNESMANN Aktiengesellschaft Verfahren und Vorrichtung zur Herstellung von Sinterteilen
US5753055A (en) * 1996-11-05 1998-05-19 Standard Car Truck Company Process for austempering ductile iron
EP1029098A1 (de) * 1997-10-14 2000-08-23 Camcast Industries Pty. Ltd Eisenlegirung mit molybdän
EP1029098A4 (de) * 1997-10-14 2002-02-27 Camcast Ind Pty Ltd Eisenlegirung mit molybdän
FR2839727A1 (fr) * 2002-05-14 2003-11-21 Technologica Sarl Procede d'elaboration et de mise en forme de pieces en fonte a graphite spheroidal a caracteristiques mecaniques elevees
WO2003100107A1 (fr) * 2002-05-14 2003-12-04 Technologica Procede d'elaboration et de mise en forme de pieces en fonte a graphite spheroidal a caracteristiques mecaniques elevees
CN100378240C (zh) * 2002-05-14 2008-04-02 科技有限公司 具有改进的机械性能的球墨铸件的制造和成形方法
EP1566459A2 (de) * 2004-02-12 2005-08-24 Technologica Sarl Verfahren zur Herstellung von Gussteilen aus Kugelgraphit mit hoher geometrischen und dimensionalen Genauigkeit und mit verbesserten mechanischen Eigenschaften
EP1566459A3 (de) * 2004-02-12 2007-06-27 Technologica Sarl Verfahren zur Herstellung von Gussteilen aus Kugelgraphit mit hoher geometrischen und dimensionalen Genauigkeit und mit verbesserten mechanischen Eigenschaften
FR2866351A1 (fr) * 2004-02-12 2005-08-19 Technologica Sarl Procede de fabrication de pieces en fonte a graphite spheroidal de grande precision geometrique et dimensionnelle et a caracteristiques mecaniques ameliorees
WO2011042123A1 (de) * 2009-10-05 2011-04-14 Bayerische Motoren Werke Ag Gusseisen-gussteil und verfahren zu dessen herstellung
CN102575326A (zh) * 2009-10-05 2012-07-11 宝马股份公司 铸铁铸件和用于生产铸铁铸件的方法
EP2471960A1 (de) * 2010-12-30 2012-07-04 Casa Maristas Azterlan Verfahren zur Herstellung einem Kugelgraphit-Gusseisenteil
US10337089B2 (en) 2014-07-25 2019-07-02 Ford Global Technologies, Llc Process for producing a component made of heat-treated cast iron
CN110561405A (zh) * 2018-06-05 2019-12-13 精工爱普生株式会社 机器人、齿轮装置以及齿轮装置的制造方法
CN110561405B (zh) * 2018-06-05 2022-12-02 精工爱普生株式会社 机器人、齿轮装置以及齿轮装置的制造方法
CN112609054A (zh) * 2020-11-09 2021-04-06 广西玉柴机器股份有限公司 一种耐疲劳气缸盖的工艺方法
CN116574874A (zh) * 2023-04-15 2023-08-11 盐城震业机械股份有限公司 一种等温淬火球墨铸铁的制备方法

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