US3670558A - Rapid thermal analysis method for predicting nodular iron properties - Google Patents

Rapid thermal analysis method for predicting nodular iron properties Download PDF

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US3670558A
US3670558A US147836A US3670558DA US3670558A US 3670558 A US3670558 A US 3670558A US 147836 A US147836 A US 147836A US 3670558D A US3670558D A US 3670558DA US 3670558 A US3670558 A US 3670558A
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curve
sample
cast iron
curve segments
iron
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Edward F Ryntz Jr
John F Janowak
John F Watton
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Motors Liquidation Co
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General Motors Corp
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    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N25/00—Investigating or analyzing materials by the use of thermal means
    • G01N25/02—Investigating or analyzing materials by the use of thermal means by investigating changes of state or changes of phase; by investigating sintering
    • G01N25/04—Investigating or analyzing materials by the use of thermal means by investigating changes of state or changes of phase; by investigating sintering of melting point; of freezing point; of softening point
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N33/00—Investigating or analysing materials by specific methods not covered by groups G01N1/00 - G01N31/00
    • G01N33/20—Metals
    • G01N33/202—Constituents thereof
    • G01N33/2022—Non-metallic constituents
    • G01N33/2025—Gaseous constituents
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N1/00—Sampling; Preparing specimens for investigation
    • G01N1/02—Devices for withdrawing samples
    • G01N1/10—Devices for withdrawing samples in the liquid or fluent state
    • G01N1/12—Dippers; Dredgers
    • G01N1/125—Dippers; Dredgers adapted for sampling molten metals

Definitions

  • a comparison of the characteristic curve segments with respective families of like curve segments obtained from samples of known metallurgical properties yields one like curve segment from each family most like each characteristic curve segment. Correlation of most like curve segments with a known relationship between said families and nodular iron metallurgical properties yields the largest range of properties possible for the unknown sample on solidification.
  • This invention relates to the production of nodular cast iron, and specifically, to a method of reliably predicting the cast structure of nodular iron from cooling curves in a foundry control operation. More specifically, this invention relates to a method of predicting, before the casting thereof, the microstructural and compositional properties of cast nodular iron.
  • control of these process variables is important to the production of acceptable nodular iron castings due to their effect on the microstructural and compositional properties of the resulting castings, e.g., percent nodularity, percent carbides, percent ferrite and pearlite, and the percent carbon, silicon and magnesium which are related to the physical properties of the castings, e.g., tensile strength and ductility.
  • the base gray iron is treated in batches with test samples poured from each bath, cooled, and the microstructure examined metallographically to determine whether the treatments have been successful. ldeally, once a successful treatment schedule has been established in the foundry, its use should result in reproducible casting quality. However, the sensitivity of nodular iron production to these variables and the processing difficulties inherent in a production operation preclude such a practice. Consequently, to insure high quality castings, commercial castings are also poured with a test sample portion which is cut from the casting and examined metallographically to detennine the microstructure of the casting. Failure to achieve an acceptable spheroidal graphitic structure in the sample means that the castings are unacceptable and must be scrapped.
  • the temperature at which the heat liberated when the austenite starts to precipitate producing an isothermal arrest in the cooling curve may be determined.
  • This temperature is the liquidus thermal arrest temperature.
  • the measurement of the liquidus thermal arrest is a reliable method of chemical analysis.
  • absolute values of temperature and time are dependent on many influencing factors which cause the curve to shift to different temperatures and times. These factors include small changes in chemical composition, the heat transfer characteristics and mass of the solidifying sample, and the accuracy of positioning a thermocouple and determining temperatures. For example, small changes in chemical composition of nodular iron samples shift the temperatures at which solidification reactions occur due to the sloping regions of the temary'iron-carbon-silicon phase diagram.
  • the present invention thus provides a method of thermal analysis which relies primarily on the shape of the entire nodular iron cooling curve rather than solely on the absolute temperature at which the liquidus then'nal arrest occurs. Furthermore, by analysis of the subtle changes in shape of the cooling curve, as hereinafter fully explained, specific microstructural and compositional properties of the nodular iron on solidification may be predicted accurately and reliably before the casting thereof.
  • a sample of molten cast iron from the holding furnace or ladle after the molten cast iron has been suitably inoculated with magnesium and ferrosilicon.
  • the sample is of such a size and thermal mass as to allow for cooling from the molten region at about 2,300 F into the solid region at about l,850 F in less than 4 minutes thereby providing a rapid analysis technique.
  • the sample, after extraction, is allowed to cool and a thermocouple which extends to the center of the sample continuously measures the change in temperature of the sample with time whereby a cooling curve for the sample is generated. This cooling curve is then divided into characteristic curve segments indicative of the nucleation and growth reactions occurring during solidification of the sample.
  • a family of like curve segments obtained in like manner from nodular iron samples of known composition and microstructure are provided.
  • a series of curve segments representing that member of each family most like each unknown curve segment is determined.
  • This determination and further comparison with a known relationship between the families of curve segments and nodular iron metallurgical properties yields the largest range of microstructural and compositional properties possible for the sample of nodular iron based upon the total number of known curve segments. It will be seen that the present invention offers a rapid thermal analysis method which predicts many of the important microstructural and compositional properties of the cast iron and provides a reliable basis on which to accept or reject the heat of molten cast iron.
  • FIG. 1 is a schematic illustration of the sampling technique for extracting a sample from a heat of molten cast iron with the millivolt data from a thermocouple immersed in the sample being fed to a recorder;
  • FIG. 2 is a cross-sectional view of the sampling device employed in this invention.
  • FIG. 3 is a reproduction of an actual cooling curve for a hypoeutectic cast iron generated in accordance with this invention.
  • FIG. 4 is a reproduction of an actual cooling curve for a hypereutectic cast iron generated in accordance with this invention.
  • FIG. 5 is an illustration of families of known curve segments.
  • FIG. 6 is a table used for correlating the unknown curve segments with the families of known curve segments shown in FIG. 5.
  • a heat of molten cast iron 10 suitably treated with magnesium and ferrosilicon is contained in a suitable holding vessel 12 at a temperature of about 2,600 F immediately prior to the pouring operation.
  • a sampling device 14, shown in detail in FIG. 2 is immersed in the holding vessel 12 allowing the molten cast iron 10 to flow through side holes 16 into the sampling device 14 activating a thermocouple 18 whose sensing junction 19 is located at the thermal center of the sample. After soaking for a few seconds to obtain thermal equilibrium, the sample is removed and air cooled through the eutectic temperature.
  • thermocouple leads 20, 22 are connected to a standard strip chart recorder 24 which continuously plots the change in temperature of the cast iron sample as sensed by the thermocouple 18 with time while the sample cools from its molten state to solid state to produce a cooling curve of the cast iron sample extending from about 2,300 F to l,850 F.
  • the size and design of the sampling device 14 is critical to generating a cooling curve which will not mask the nucleation and growth reactions occurring in the solidifying cast iron sample but which will provide sensitivity to inflections and arrests in the cooling curve resulting from the reactions occurring on solidification and which will cool sufficiently fast to provide the required temperature data, preferably in less than four minutes.
  • the critical features of the cast iron sample and the sampling device are: sample means and soundness, sample surface area-towolume ratio which determines the cooling rate, the wall thickness and material of the sampling device, and the position of the thermocouple in the sampling device. These features are important in obtaining cooling curves which are responsive to changes in nodular iron processing which in turn afiect the resulting microstructure.
  • the microstructure of the sample will not be indicative of the microstructure encountered in typical castings. For example, possible carbide formation and high graphite nodule counts will result from significantly smaller samples. If the sample is inordinately large resulting in a slow cooling rate, sensitivity to small inflections in the cooling curve representing variations in the microstructure will be lowered or masked. In addition, a slower cooling rate extends the time required in obtaining and analyzing the cooling curve which could result in low pouring temperatures and unacceptable castings.
  • the preferred form of the sampling device is 1 inch in inside diameter, 1% inch in outside diameter, and is 3 inches in height.
  • the device is made from a low carbon-low sulphur steel and provides a receiving basin 26 1 inch in diameter by 1% inch high.
  • the two side holes 16 limit the height of the molten metal sample in the receiving basin 26.
  • the thermocouple assembly 18 is formed of 24.gauge Chromel-Alumel thermocouple wires 20,22 insulated with a suitable ceramic 28 and sheathed in 3mm diameter Vycor tube 30.
  • the thermocouple wires 20, 22 terminate in a sensing junction 19 which is located at the thermal center of the molten metal sample in the receiving basic 26.
  • thermocouple assembly is cemented in a ceramic sleeve 32 and the ther-' mocouple wires 20, 22 extend to a cardboard tube 34 which supports the thermocouple wires 20, 22 and allows for a quick connect and disconnect of the respective wires 20, 22 with the recorder 24.
  • Metal clipping portions 36 serve to position and hold the thermocouple assembly in the receiving basin 26.
  • FIGS. 3 and 4 there is reproduced actual cooling curves of a sample of a hypoeutectic casting iron and a hypereutectic cast iron, respectively, obtained in accordance with the present invention. That is, the sampling device 14 shown in FIG. 2 was immersed in a heat of molten cast iron held at a temperature of about 2,600 F. Upon immersion, the molten cast iron flowed through the side holes 16 filling the receiving basin 26. The sampling device was held in the molten cast iron for a few seconds until a thermal equilibrium was established as indicated by the thermocouple 18 surrounded by molten metal recording an equilibrium temperature.
  • thermocouple sensing junction 19 when constructed in accordance with the foregoing description, would be located at the approximate thermal center of the sample.
  • the sample was then air cooled from the holding temperature of 2,600 F.
  • a cooling curve was generated for the sample from a temperature of about 2,300" F to a temperature of about l,850 F at which temperature the sample was completely solidified. As shown in FIGS. 3 and 4, the cooling time was about seconds.
  • thermocouple sensing junction 19 continuously sensed the temperature change of the sample registering the thermal arrest and other thermal effects indicative of the various reactions taking place in the sample as the sample solidified.
  • This temperature response data was plotted on a standard strip chart recorder 24 as a function of time to provide a cooling curve for the cast iron sample.
  • the cooling curves were then divided into characteristic curve segments indicated by numerals II, III and IV. Reference points have been placed on the curves at curve inflection points for purposes of the following description. As hereinafter more fully explained, these curve segments are indicative of the primary nucleation and growth reactions occurring on solidification of the sample.
  • Recalescense is indicated in region II of FIG. 4 by a temperature increase 40 caused by the rapid liberation of the latent heat of transformation. If for some reason the treatments were not effective, this section of the curve is displaced downwardly. This suppression of the curve has been related to increasing quantities of vermicular and flake graphite and carbides. A reversion of the graphite spheroids to essentially flake morphology also produces a recalescense in this section of the cooling curve. However, the curve segment becomes extended under these conditions. This deteriorated structure also produces characteristic changes in regions Ill and IV as discussed below.
  • the bulk eutectic arrest 42 during which the major portion of growth occurs is represented by region III.
  • region III For a eutectic/hypereutectic iron this section of the cooling curve has been related to the presence of carbides which form when the eutectic arrest temperature falls below the metastable eutectic temperature. The tendency to carbide formation results from insufficient post-inoculation or face of the post-inoculation effect. An undercooling or rapid decrease in temperature in this curve section indicates that metastable iron carbide solidification has occurred. If the post-inoculation is sufficient to maintain solidification in the iron-graphite system, the temperature decrease in this area is represented by a gradual slope in the curve.
  • This knee 44 of the curve exhibits a large angle between the curve sections for well-formed graphite spheroids in both hypoeutectic and eutectic/hypereutectic irons.
  • the large angle between the bulk eutectic arrest 42 and the slope of the curve at point 5 is believed to result from decreased growth rates caused by the time dependent diffusion of carbon through the increasing austenite shell to the graphite nodule. Small angles between the line segments indicate carbide formation and/or a low percent nodularity.
  • region III When region III exhibits large undercooling, sharp angles occur in region IV indicating that the last stages of growth occurred rapidly by massive carbide reaction rather than by a diffusion reaction required for complete graphitization.
  • the formation of flake graphite produces a recalescense in region IV indicated by small angles which results from graphite growing in direct contact with the melt. As with carbide formation, this reaction does not require a continuing decreasing temperature to occur.
  • Hypereutectic nodular iron cooling curves also have an initial arrest 48 above the bulk eutectic arrest occurring in region III, as shown in FIG. 4 between points 2 and 3.
  • the similarity between a hypoeutectic cooling curve of high nodularity and a eutectic/hypereutectic cooling curve of very high carbide content requires a method of differentiation.
  • the temperature at which the initial arrest occurs has proven to be an adequate criterion for separating the two solidification modes, i.e., as the iron composition becomes increasingly hypoeutectic, the initial arrest occurs at higher temperatures.
  • high carbide contents as indicated by region III of the curve also tends to lower the initial arrest temperature.
  • each of these characteristic cooling curve regions is representative of either graphite or matrix structures, the interrelationship of these regions must be considered in evaluating the curve to predict microstructure. Accordingly, as shown in FIG. 5, a family of curve segments II, III, and IV is provided for each of the characteristic curve segments II, III and IV shown in FIGS. 3 and 4. The curve segments shown in region 1 of FIG. 5 are not used for comparison with the curve segments I in FIGS. 3 and 4 in the same manner as those of families II, III and IV of FIG. 5. Rather they are used to determine the minimum temperature 46 just prior to inflection point 2 to differential hypoeutectic solidification from hypereutectic solidification.
  • .region I has not been designated as a "characteristic curvesegment'," as used herein, and has been labeled with a subscript T to indicate temperature dependence.
  • characteristic curvesegment' As used herein, it is possible, however, to differentiate the solidification modes by an analysis of curve shapes occurring in region I in the same manner as regions II, III, and IV. It will be noted that it is not critical to the practice of this invention that the cooling curves be divided into these regions only. Rather the curve can be divided into more regions determined by the maxima, minima and inflection points occurring in the curve depending on the accuracy of prediction required. However, there must be a family of curve segments corresponding to each characteristic curve segment of the cooling curve for prediction of the microstructural and compositional properties of the cast iron. We have found that the divisions shown in FIGS. 3, 4 and 5 and previously described identify the primary nucleation and growth reactions occurring on solidification and provides good predictability.
  • FIG. 5 represents a compilation and analysis of over cooling curves obtained from nodular irons representing a wide range of chemistries and microstructures.
  • each of the characteristic curve segments in FIGS. 3 and 4 there is provided a family of like curve segments. obtained from samples of known composition and microstructure with each like curve segment in each of the families being related to a known range of microstructural and compositional properties.
  • these regions must be correlated to predict the largest possible range of properties mutually related to each serial combination of like curve segments of the respective families.
  • FIG. 6 is a tabular correlation which provides such an interrelationship of curve families for three properties of primary importance in nodular iron production-percent nodularity, carbon equivalent, and percent carbides.
  • a range is shown on the horizontal across the top of the table and the designation of curve families I II, III and IV of FIG. is shown on the vertical at the left of the table.
  • the table is compiled by determining from the known samples the range of properties possible for the shape of each curve segment in each family. For example, curve H (curve segmgrt l ljn region I, of FIG.
  • curve segment A is known to indicate a nodularity of 50-95 percent
  • curve segment A is known to indicate a nodularity of 85-95 percent
  • curve segment A is known to indicate a nodularity of 90-95 percent
  • curve segment A is known to indicate a nodularity of 85-95 percent.
  • This process can be repeated for each possible serial combination of curve segments of each family for each property under consideration to produce a composite curve for each serial correlation of a curve segment chosen from each family.
  • the cooling curve of an unknown sample can be compared to find the one most like it in shape for each property whereby the properties of the unknown sample may be predicted.
  • this process is inordinately time-consuming and, therefore, the serial correlations of curve families has been broken down into tabular form in FIG. 6.
  • the curve of the actual hypoeutectic iron sample was divided into regions characteristic of the primary nucleation and growth reactions occurring on solidification.
  • the characteristic curve segments in regions II, III, and IV were compared with the spectrum of curves in the corresponding families of FIG. 5 to determine the member most like the respective segments.
  • the curve segments in region I, of FIG. 5 were used only to determine the minimum temperature 46 just prior to the second inflection point in order to differentiate hypoeutectic and hypereutectic solidification as previously described. Starting from a reference point of 2,300 F, it may be seen that this minimum temperature occurred at about 2,070 F which corresponds to area H of FIG. 5. Comparing regions II, III, and IV of FIG.
  • H indicates a nodularity of 50-95 percent
  • F indicates a nodularity of 40-60 percent and -90 percent
  • K indicates a nodularity of 80-85 percent
  • F indicates a nodularity of 40-90 percent.
  • the four in serial combination indicate that 80-85 percent is the largest range of nodularities common to all four.
  • a like analysis may be made for carbon equivalent (CE) and percent carbides, however, for percent carbides only regions II, III, and IV need be considered. Repeating the process for the serial combination H F Km, F 'carbon equivalent (CE) in the range of 4.56-4.60 and percent carbides in the range of 5-10 percent is predicted. Actual metallographic analysis showed the cast iron sample to be of 90 percent nodularity and 8 percent carbides and to have a CE 4.44.
  • a method of predicting metallurgical properties of a molten cast iron treated to form nodular cast iron on solidification comprising the steps of:
  • said curve being obtained by continuously measuring and plotting the change in temperature with time of said sample of said iron while said sample of said iron is cooling from the molten to the solid state
  • a method of predicting microstructural and compositional properties of a molten cast iron treated to form nodular cast iron on solidification comprising the steps of:
  • a method of predicting the nodularity, carbon equivalent, and percent carbides of a molten cast iron treated to form nodular cast iron on solidification comprising the steps of:
  • said sample having a thermal mass such as to cool from about 2,300 F to l,850 F in about 0.5 to 4 minutes, allowing said sample to cool from its molten state to a solid state, generating a cooling curve of said molten cast iron sample,
  • said curve being obtained by continuously measuring and plotting the change in temperature with time of said sample of said iron while said sample of said iron is cooling from the molten to the solid state
  • each of said characteristic curve segments a respective family of like curve segments obtained in like manner from like cast iron samples of known nodularity, carbon equivalent, and percent carbides, wherein each curve segment in each of said respective families is related to a known range of nodularities, carbon equivalents, and percent carbides,
  • a method of predicting the nodularity of a molten cast iron treated to form nodular cast iron on solidification comprising the steps of:
  • said curve being obtained by continuously measuring and plotting the change in temperature with time of said sample of said iron while said sample of said iron is cooling from the molten to the solid state

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Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3882727A (en) * 1974-07-03 1975-05-13 Leeds & Northrup Co Cooling curve apparatus
US3891834A (en) * 1974-05-22 1975-06-24 Ford Motor Co Cooling curve computer
US4046509A (en) * 1970-04-27 1977-09-06 Stig Lennart Backerud Method for checking and regulating the conditions of crystallization in the solidification of melts
US4088974A (en) * 1975-01-21 1978-05-09 Zhitetsky Leonid Sergeevich Digital device for automatically checking carbon content in metal with reference to temperature stops on cooling curve
DE2821352A1 (de) * 1977-05-18 1978-11-30 Electro Nite Verfahren und entsprechendes geraet fuer die voraussage metallographischer strukturen
FR2410272A1 (fr) * 1977-11-24 1979-06-22 Ver Foerderung Giesserei Ind Procede et dispositif pour la mesure de la courbe de refroidissement d'un echantillon en metal ou en alliage metallique, particulierement en fonte ou en acier moule pour l'analyse thermique differentielle
US4164148A (en) * 1978-05-01 1979-08-14 Laforet Henry A Method for determining sulfur content of cast iron
DE2919625A1 (de) * 1978-05-17 1979-11-29 Yahagi Elect Eng Co Verfahren und vorrichtung zum schnellen vorhersagen des grads an kugelform von kugelgraphitgusseisen
FR2473177A1 (fr) * 1980-01-04 1981-07-10 Kawaso Electric Ind Co Dispositif pour determiner la teneur en carbone d'un metal en fusion
EP0107237A1 (fr) * 1982-10-11 1984-05-02 CENTRE DE RECHERCHES METALLURGIQUES CENTRUM VOOR RESEARCH IN DE METALLURGIE Association sans but lucratif Procédé pour le contrôle automatique de la structure des produits en acier laminés
DK150996B (da) * 1976-07-09 1987-10-05 Pechiney Aluminium Digel til termisk analyse af aluminiumlegeringer under deres stoerkning
EP0327237A3 (en) * 1988-02-05 1990-08-16 Bcira A method of testing the magnesium content of magnesium-treated cast iron
ES2259937A1 (es) * 2005-04-15 2006-10-16 Casa Maristas Azterlan Metodo para la determinacion de la tendencia al rechupe de una fundicion grafitica esferoidal.
EP2090670A1 (en) * 2007-12-05 2009-08-19 Casa Maristas Azterlan Method for predicting spheroidisation degree in defined zones of spheroidal graphitic cast iron pieces
WO2013013681A1 (de) * 2011-07-22 2013-01-31 Neue Halberg Guss Gmbh Verfahren zur herstellung von gusseisen mit vermiculargraphit und gussteil
CN115684533A (zh) * 2022-09-27 2023-02-03 中机生产力促进中心有限公司 球墨铸铁乏燃料运输容器铸件的评定方法

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Publication number Priority date Publication date Assignee Title
GB8329622D0 (en) * 1983-11-05 1983-12-07 Systematic Micro Ltd Temperature monitoring system

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Publication number Priority date Publication date Assignee Title
US3455164A (en) * 1966-07-06 1969-07-15 Leeds & Northrup Co Immersion molten metal sampler
US3463005A (en) * 1966-07-12 1969-08-26 Leeds & Northrup Co Immersion molten metal sampler device

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3455164A (en) * 1966-07-06 1969-07-15 Leeds & Northrup Co Immersion molten metal sampler
US3463005A (en) * 1966-07-12 1969-08-26 Leeds & Northrup Co Immersion molten metal sampler device

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4046509A (en) * 1970-04-27 1977-09-06 Stig Lennart Backerud Method for checking and regulating the conditions of crystallization in the solidification of melts
US3891834A (en) * 1974-05-22 1975-06-24 Ford Motor Co Cooling curve computer
US3882727A (en) * 1974-07-03 1975-05-13 Leeds & Northrup Co Cooling curve apparatus
US4088974A (en) * 1975-01-21 1978-05-09 Zhitetsky Leonid Sergeevich Digital device for automatically checking carbon content in metal with reference to temperature stops on cooling curve
DK150996B (da) * 1976-07-09 1987-10-05 Pechiney Aluminium Digel til termisk analyse af aluminiumlegeringer under deres stoerkning
DE2821352A1 (de) * 1977-05-18 1978-11-30 Electro Nite Verfahren und entsprechendes geraet fuer die voraussage metallographischer strukturen
FR2410272A1 (fr) * 1977-11-24 1979-06-22 Ver Foerderung Giesserei Ind Procede et dispositif pour la mesure de la courbe de refroidissement d'un echantillon en metal ou en alliage metallique, particulierement en fonte ou en acier moule pour l'analyse thermique differentielle
US4164148A (en) * 1978-05-01 1979-08-14 Laforet Henry A Method for determining sulfur content of cast iron
DE2919625A1 (de) * 1978-05-17 1979-11-29 Yahagi Elect Eng Co Verfahren und vorrichtung zum schnellen vorhersagen des grads an kugelform von kugelgraphitgusseisen
US4333512A (en) * 1978-05-17 1982-06-08 Yahagi Iron Co., Ltd. Method of quickly predicting the degree of nodularity of spheroidal graphite cast iron from a molten iron sample
FR2473177A1 (fr) * 1980-01-04 1981-07-10 Kawaso Electric Ind Co Dispositif pour determiner la teneur en carbone d'un metal en fusion
EP0107237A1 (fr) * 1982-10-11 1984-05-02 CENTRE DE RECHERCHES METALLURGIQUES CENTRUM VOOR RESEARCH IN DE METALLURGIE Association sans but lucratif Procédé pour le contrôle automatique de la structure des produits en acier laminés
EP0327237A3 (en) * 1988-02-05 1990-08-16 Bcira A method of testing the magnesium content of magnesium-treated cast iron
ES2259937A1 (es) * 2005-04-15 2006-10-16 Casa Maristas Azterlan Metodo para la determinacion de la tendencia al rechupe de una fundicion grafitica esferoidal.
ES2259937B2 (es) * 2005-04-15 2007-06-16 Casa Maristas Azterlan Metodo para la determinacion de la tendencia al rechupe de una fundicion grafitica esferoidal.
EP2090670A1 (en) * 2007-12-05 2009-08-19 Casa Maristas Azterlan Method for predicting spheroidisation degree in defined zones of spheroidal graphitic cast iron pieces
WO2013013681A1 (de) * 2011-07-22 2013-01-31 Neue Halberg Guss Gmbh Verfahren zur herstellung von gusseisen mit vermiculargraphit und gussteil
CN115684533A (zh) * 2022-09-27 2023-02-03 中机生产力促进中心有限公司 球墨铸铁乏燃料运输容器铸件的评定方法

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