• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    PCT No. PCT/SE85/00339 Sec. 371 Date May 7, 1986 Sec. 102(e) Date May 7, 1986 PCT Filed Sep. 10, 1985 PCT Pub. No. WO86/01755 PCT Pub. Date Mar. 27, 1986.Method for producing castings from cast-iron containing structure-modifying additives. A sample from a bath of molten iron is permitted to solidify during 0.5 to 10 minutes. The temperature is recorded simultaneously by two temperature responsive means, one of which is placed in the center of the sample and the other in the immediate vicinity of the vessel wall. The dispersion degree of the graphite phase is assessed in relation to known reference values by aid of recorded values of supercooling at the vessel wall, the recalescence at the vessel wall, the difference between the temperature at the vessel wall and at the centrum of the vessel and the derivative of the temperature decrease at the vessel wall during the time of constant eutectic growth temperature at the center. When necessary a graphite nucleating agent is added to the molten bath or the dispersion is lowered by implementing a holding time prior to casting. The morphology of the graphite precipitation is also determined by aid of recorded values and possibly corrected by changing the amount of structure-modifying agents present.
    公开号:SU1741617A3
    申请号:SU874202164
    申请日:1987-03-11
    公开日:1992-06-15
    发明作者:Леннарт Бекеруд Стиг
    申请人:Синтер-Каст Аб (Фирма)；
    IPC主号:
    专利说明:

    flax material at the vessel wall, recalescence at the vessel wall (rekv). positive difference between the temperature at the named wall and in the center of the selected amount (AT +) and the temperature gradient in the sample behind the front of the eutectic growth, expressed as () (Tc max)
    (approximately constant for at least a short period of time during the growth of the eutectic in the center of the selected quantity () from 0), arbitrarily
    Ss c
    expressed in the form of the largest negative values (DTmax) of the temperature difference, including when the molten bath has an insufficient number of crystallization centers, an agent is introduced into it that increases the nucleation of graphite. When it is found that the crystallization centers are in excess, the latter decreases. The morphology of graphite release is determined by known reference values applied to the same sampling method using a crystallization temperature at the center of the bath (Tc), recalescence at the center (rekc) and at the maximum growth temperature (Tc max). The amount of modifying agent structure present is adjusted so that graphite during solidification of the cast iron melt is released in a worm-like form after casting.
    FIG. 1 is a graph containing a solidification diagram derived from measurements of values obtained in the production of worm-like cast iron; Figures 2-4 are various examples of sampling vessel variants suitable for use in carrying out the method.
    FIG. Figure 1 shows the temperature (T) and time (t) curves, of which curve I shows the course of solidification near the wall of the sampling vessel, and curve II shows the process of solidification in the center of the sample in the vessel.
    Points ai, 32 denote a decrease in temperature per unit time due to the heat released during the formation of the primary austenitic phase. Point b on curve II illustrates the moment at which austenite crystals (in dendritic (branched) form) were formed in the entire amount selected. Subsequently, the molten material of the sample between austenitic crystals is enriched with carbon (and other alloying elements), so that gradually with a further decrease in the
    temperature in the sample is reached eutectic composition.
    The point in on curve I denotes the moment at which the drop in temperature stops. Graphite crystals form on the vessel wall with sufficient supercooling, and these graphite crystals grow with the iron phase in the eutectic mixture. After this stage, during melting, the molten sample is reheated (by recalescence) to the equilibrium temperature of the eutectic mixture in FIG. 1 (it is indicated by dashed TEU lines). However, at this early stage
    5, a steady state of growth is still not fully achieved due to growth suppression mechanisms, and the speed with which recalescence occurs essentially means the number of active graphite nuclei per unit volume. Similarly, the point r on curve II denotes the maximum supercooling Tc, point e - the recalescence curve; Point e is the usual temperature of growth at an established stage in the center of the sampling vessel. These data provide information on the growth mechanism at the eutectic solidification stage.
    The wall temperature represents an instant image of the crystallization in a limited volume of molten material (thin wall), and the temperature at the center of the vessel is an integral image of the thermal behavior.
    5 total internal sample volume. The temperature along the radius in the sampled amount between the two measurement points includes a temperature wave that propagates forward and reflects
    0 sequence of growth along the inside of the eutectic solidification. This means that the loaded thermoelement registers the solidification process corresponding to the process in
    5 thin-walled castings, when, as a central thermoelement, provides information relating to the nature of solidification in thick parts of the casting. Only by considering such combined information can a conclusion be drawn regarding the possibility of the molten material to form the required structure in castings of various thickness during the processes of casting and solidification,
    The description of the solidification processes mainly relates to the eutectic compositions of cast iron. However, the method can also be applied to the cast iron of eutectic and hypereutectic compositions. When the eutectic composition hardens, no primary crystals grow, and in the case of hypereutectic compositions it occurs, but only in the form of primary graphite precipitates.
    It was experimentally found that with insufficient hypothermia, weak recalescence, and high growth temperature prevailing during the solidification process, flaky graphite is formed.
    If the supercooling temperature is high, the recoil is low and the growth temperature is low, then the graphite solidifies in a spherical form, the result is cast iron with a spherical shape of graphite.
    When vermicular graphite is released during solidification, there is a strong overcooling, a strong recalescence and a high growth temperature.
    The deviations shown by the curves are sufficient to make accurate conclusions for these main groups, as a result, it is possible to predict the formation of ceraform graphite with a high degree of accuracy, which in turn makes it possible to control the process within narrow limits.
    Assuming that the external conditions remain the same from case to case, a comparison can be made between the two quantities recorded by the temperature measurement devices located near the wall of the sampling vessel and in the center of the melted quantity taken, and between different tests of the molten bath. It is necessary that the differences in technique and geometry of the sampling vessel and the material placed in it be so small that reproducible and comparable results can be obtained for different samples.
    A number of sample vessels suitable for use in solidification tests. described in FIG. 2-4 The applied methodology should be the same for each sample or for each test so that the temperature equilibrium between the molten material and the sample vessel is reached. The temperature around the sampling vessel is adjusted so that the heat is lost by the sampling vessel of the process that allows the molten material to solidify for 0.5-10 minutes. The lower limit depends on the fact that a faster cooling rate leads to the formation of cementite in accordance with the metastable chart. Slower cooling than 10
    mines are impractical in terms of performance and, in addition, the accuracy of the measured results deteriorates due to other reactions taking place around the vessel and due to convection. The ideal cooling period is 2-4 minutes. The dimensions of the sampler or test vessel are not so critical, although for practical reasons the diameter of the vessel
    0 must be at least 2 and not more than 10 cm. A suitable diameter is 3-6 cm. It is convenient to fill the vessel to a height of several centimeters. The height of the full sample must be greater than its diameter. It is preferable5 that the heat from the sampling vessel recedes mainly in the radial direction. This can be achieved by isolating the upper and lower surfaces of the selected amount.
    0
    The release of latent heat and the growth of the eutectic front (which depends on the appropriate growth mechanism) and the thermal conductivity of the solidified layer,
    5 located behind the front, to a greater degree depend both on the number of graphite crystals in the eutectic structure and on the shape of the crystals mentioned. A suitable method for determining this complex function is 0 / T -.
    is determined by the slope (), by (A
    radiated during solidification by acting on a temperature measuring device located near the vessel wall for the period during which the temperature measuring device located in the center of the vessel records the plateau temperature corresponding to the temperature of the eutectic stage Tc max period-, and T h yes the time during which ()
    equals zero. This complex function can also be determined by measuring
    5 maximum difference (DTmax) between two curves during the solidification process. It has been found that in both cases the values change for different forms of graphite in the iron. Gray cast iron comprising
    0 flaky graphite, gives small temperature differences between the two solidification curves. Spherical cast iron shows large DTmax values, whereas cast iron hardening in the form of worm-like cast iron gives values between them, which provides a good opportunity for differential assessment of the properties of the corresponding molten baths during solidification.
    In the eutectoid transformation (in the solid phase from austenite to ferrite and cementite, point w speed and, consequently, the final structure can be examined in detail by comparing deviations from two measured points, especially by comparing the displacement time and the magnitude of the derived functions.
    In addition to the possibility of recording double solidification curves from an unknown sample and comparing the configurations of these curves with the corresponding curves obtained from samples with known crystal characteristics (either graphically or by any other recording method, for example, a digital processor), the following properties are characteristic upon receipt of pig iron containing graphite, which hardens in worm-like form.
    The most reliable way to determine the worm-like growth is to use for this purpose supercooling in the center (Tc), recalescent sequence (rekc) and maximum temperature of the eutectic growth
    (Tc max).
    The actual degree of dispersion (defined here as the number of graphite crystals per unit volume) can be determined using the recalescent sequence at the wall (rekv),
    A-rYa T h-r
    PBX max OR OTHER--) with TC max software
    M. V
    temperature curve of the initial stages of eutectic formation.
    The initial stages of eutectic formation usually occur when the degree of supercooling is Tu, but with very efficient formation of graphite, the delay on the cooling curves shows the formation of small amounts of flaky graphite.
    All of the enumerated values can be measured with accuracy and reproducibility, which makes it possible to evaluate crystallization properties characteristic of the molten bath, standard curves with recorded curves based on measuring the obtained values, although these values can also be compared in digital form using automatic processing data.
    In order to clarify these various possibilities, FIG. 1 illustrates graphic curves on which two curves are plotted with a difference in time g: curve I minus curve II AT (here the region of positive values of DT is shown by hatching); for two curves, (-) is constructed, where
    CX t /
    These values are given as l-derivatives rekv and hex (shown with shaded
    areas of positive values.
    Thus, it is possible to read from the graphic curves those measurements that must be taken in order to obtain the desired result, and then, in order to show,
    0 that the required results should be achieved arbitrarily or by taking additional samples or performing additional tests. Knowledge of the crystallization properties of molten
    The bath 5 allows for the necessary additions or necessary deletions of the respective substances. The experience is to measure the crystallization properties of perfectly
    0 automatically, and then automatically adjust the composition of the molten bath with the help of programming technology to get worm-like cast iron. The rate of solidification depends on the thermal conductivity of the vessel wall, wall thickness, the ratio of the volume and surface of the sample and the surrounding temperature. Although all of these parameters may vary, they must be adapted so that
    0 to enable the sampling or testing method to be carried out in a practical manner, as well as adapted for predetermined castings of various sizes.
    The sampling vessel is cooled at
    5 at room temperature, although it is possible to prolong the solidification process, the solidification takes place in a furnace at a temperature between the melting point of the iron and the surrounding temperature. Solidification time also
    0 can be extended by isolating the sample vessel or by placing the vessel in an insulating jacket during the solidification process. If desired, the solidification process can be
    5 is also accelerated by air cooling, fog spray, or any other similar method.
    Before starting the measurement process, the entire device, the sampling vessel, the temperature chamber and the molten material present must be in temperature equilibrium with the temperature above the melting point of the sample. It is approximately 1200-1400 ° C.
    5 in the case of cast iron.
    An equilibrium state can be achieved, for example, by manufacturing a sampling vessel together with a device measuring the temperature, which allows them to be immersed in a molten bath heated to a temperature of about 1200-1400 ° C and kept in the bath until the whole device is heated to temperature, and then remove from the bath and produce cooling. In this case, the temperature measuring device is connected to some kind of recording device, which records the measured data in analog or digital form.
    FIG. Figure 2 shows a sampling or test vessel for immersion in a hot molten bath. This vessel is a body 1 of refractory material (suitable ceramic material). The housing 1 is connected to the tubular element 2, with which the vessel can be held and immersed in a bath. The housing 1 is provided with a hole 3 through which molten material can flow into the housing. In case 1 two thermoelements 4 and 5 are provided. One of which is located in the immediate vicinity of the wall of the case (4), and the other (5) in the center of the case. Thermocouples are connected to a recording device (not shown) using conductors 6
    FIG. Figure 3 shows another preferred sample or test vessel that can be filled with hot material to produce an analysis. The vessel of this option is a body 7 with temperature measuring devices 8 and 9 introduced through its bottom. One (8) of these measurements The temperature devices are located next to the wall of the body and the other (9) is located in the center of the body. The vessel is surrounded by a heating coil 10 to preheat the vessel. The temperature measuring devices 8 and 9 are connected to recording devices (not shown) using wires 11
    FIG. 4 shows another variant of a sampling or test vessel, which is the body 12, which is surrounded by a high-frequency heating device 13 for re-heating the vessel and the samples contained therein. The molten material can be fed into the vessel using a ladle. The housing 12 is arranged to cooperate with the lid 14 provided with guides 15 for placing the lid on the housing 12 and temperature measuring devices 16 and 17 that are connected downwards and which are connected to a recording device (not shown) using wires 18. A lid carrying temperature measuring devices is placed on housing 12 after heating the vessel and the sample contained therein to the required temperature.
    In the practical implementation of the method, a conventional molten iron bath is prepared, the chemical composition of which is adjusted to the required values in accordance with chemical analysis. A sample is then taken from the bath for thermal analysis according to the invention and
    0 record the solidification curves. The existing nucleating ability of the molten bath is evaluated. In order to obtain the primary germinative capacity,
    5 necessary additives of oxide-sulfide-forming agents. Examples of suitable oxide and sulfide-forming additives include calcium, aluminum and magnesium. Another prerequisite for the formation of graphite nuclei is. so that the carbon equivalent of an UE would be high enough. Consequently, nucleation can be facilitated by introducing a substance that
    5 increases the carbon equivalent (RE), for example, ferrosilicon, quartz or silicon carbide. Although the introduction of nucleating agents is well known in the industry, it was not possible before
    It is necessary to establish with sufficient accuracy the need for the production of such additives before casting.
    After system calibration by function
    5 TV. rekv and DT receive specific important information regarding nucleating ability. The lack of nucleating agents can be said to increase the supercooling. In some cases, this increase is so great that at the edges of the sampling vessel a transition to a metastable state takes place. When white cast iron hardens, extremely rapid recalescence takes place. In order for nodular cast iron to form, hundreds of times more embryos must be formed than are required to form flaky graphite. In order to obtain a worm-shaped pig, the nucleating capacity must be less than is required for the formation of spherical cast iron, suitable is a value equal to one tenth. If an extremely low nucleating capacity has been measured, a substance that stimulates nucleation can be added. If it is desirable to lower the nucleating capacity, the molten bath is simply maintained for a predetermined period of time, since the nucleating capacity decreases with increasing holding time.
    The amount of active structure-modifying substances is regulated depending on the supercooling in the center of the material (Tc), the maximum growth temperature (Tc max) and recalescence in the center of the material (rekc). When the sample is solidified, the amount of active structure modifying agents present controls the crystalline growth. When nodular graphite is formed, growth is limited in three directions when the release of graphite reaches a certain level. But if the amount of active structure-modifying substances is slightly reduced as to what is required to produce nodular graphite, then crystalline growth is limited in only two directions, leaving the opportunity for crystalline growth from the molten metal in the third direction. When such crystalline growth takes place, worm-like graphite crystals form. An analysis of these values (Tc, rekc, and Tc max) shows whether or not the molten bath contains enough structure-modifying substances. When such content is found to be insufficient, structure-modifying elements should be added. For this purpose, magnesium may be used in a possible combination with rare earth metals. for example, cerium. An extremely high content of structure-modifying substances can be reduced by oxidation, which can be accomplished by introducing oxygen into the bath or by introducing oxidizing agents, such as magnetite. Oxidation can also be carried out by keeping the metal surface in air for several minutes. In order to reduce the content of active structure modifying agents, inhibitors such as titanium can also be added to the bath.
    The present invention is directed mainly to solving the problems of controlling casting processes for solidification with worm-like precipitates.
    graphite. In addition, the method also offers various possibilities for accurately determining the degree of distribution in the production of gray iron with simultaneous control of the type of flaky graphite release. It is also possible to accurately determine the amount of structure-modifying substances and the necessary degree of dispersion in the production of spheroidal spherical cast iron, thereby making it possible to save when using expensive additives.
    The deviations in the solidification curve, obtained by measuring in the center of the sample,
    by the end of the solidification phase, they can also indicate the possibility of carbide formation, which in turn provides valuable guidance on the lack of a nucleating agent in combination with
    the presence of a carbide stabilizing element forming clusters in the microstructure,
    权利要求:
    Claims (2)
    [1]
    1. The method of automatic control of obtaining iron with a given structure,
    including the smelting of iron, its modification, selection of liquid iron with a sampler with its thermocouple junction placed in the center, thermal analysis
    cast iron, recording and automatic output of results in numerical form and in the form of curves depending on the sample solidification time, comparing the obtained results with the reference ones and subsequent adjustment of the melt by adding modifiers, characterized in that, in order to improve the accuracy of the analysis and improve express speed, the sampler near the wall of the metal reservoir additionally
    A thermocouple junction is installed, and the sampler is introduced into the analyzed melt and kept there until it reaches thermal equilibrium.
    [2]
    2. Method according to claim 1, characterized in that samples are taken from the bath of the analyzed melt and transferred to the metal receptacle of the vessel, near the wall of which an additional thermocouple junction is installed, and the molten iron in the vessel is heated to the bath temperature of the analyzed melt.
    F
    FIG. one
    Phage. 2
    12
    ZZZZZZZZ Fi.4
    Compiled by N. Kostornoy Tehred M. Morgental
    Proofreader T.Paly
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    VNIIPI State Committee for Inventions and Discoveries at the State Committee on Science and Technology of the USSR 113035. Moscow, Zh-35. Raushska nab., 4/5
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    SE8404579A|SE444817B|1984-09-12|1984-09-12|PROCEDURE FOR THE PREPARATION OF CASTING IRON|
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