JP4548263B2 - Manufacturing method of cast iron products with excellent wear resistance - Google Patents

Description

  The present invention relates to a cast iron product suitable for use in a crushing crusher for ore, rock, etc., a grinding mill, a construction machine, or a member that requires wear resistance such as a rail and various liners. It relates to improvement of wear resistance.

  Conventionally, high manganese cast steel and high chromium cast iron having excellent wear resistance have been used for members that require wear resistance such as crushers for crushing ores such as ores and rocks, and mills. High manganese cast steel usually contains C: 1.0 to 1.4% and Mn: 10 to 14%, and is used by forming a complete austenite structure by dissolving carbides by water toughening. Therefore, the high manganese cast steel exhibits excellent toughness, and also exhibits excellent wear resistance because the surface hardness increases due to work hardening caused by repeated striking or the like. However, the high manganese cast steel has a problem that it has a low yield strength compared to the tensile strength and is easily deformed. Further, since it requires a water toughness treatment, it tends to be deformed and the depth of work hardening is shallow.

  High chromium cast iron is usually cast iron containing, for example, about C: 2-3% and Cr: 15-35%, and has excellent corrosion resistance, heat resistance and wear resistance due to high Cr content. Show. However, high chromium cast iron has low toughness, and especially in castings manufactured by a method that uses a sand mold to reduce the cooling rate, austenite (γ) grains that crystallize as primary crystals become coarse, resulting in the end of solidification. In addition, the eutectic carbide produced at the grain boundaries of the primary crystal grains is coarsened, so that there is a problem that hardness, toughness, and wear resistance are also lowered.

  For such a problem, for example, Patent Document 1 proposes a method for manufacturing a high Cr wear-resistant white cast iron casting in which a high Cr cast iron melt is poured into a mold made of metal particles. According to the technique described in Patent Document 1, eutectic carbide precipitates finely, and wear resistance is improved. However, the technique described in Patent Document 1 has a problem in that it cannot exceed the mold casting product in terms of quality, and further, the tendency of occurrence of defects on the casting surface increases and the manufacturing cost increases.

  Patent Document 2 proposes an eutectic alloy-based alloy casting method such as white cast iron. The technique described in Patent Document 2 includes a step of pouring the molten alloy as a flow into the casting mold at a temperature higher than the liquidus temperature, and adding a particulate material to the flow of the molten alloy to make the molten alloy a liquidus temperature. An alloy casting method comprising a step of supercooling to a primary phase solidification temperature range between a solidus temperature and a solidus temperature. According to the technique described in Patent Document 2, the addition of the particulate material enables rapid cooling by removing heat from the molten alloy, and the particulate material acts as a primary phase nucleus, facilitating the refinement of the primary phase. It is supposed to be. However, the technique described in Patent Document 2 requires a facility for adding the particulate material during the pouring, and in addition to the problem that the manufacturing cost increases, it is difficult to add the particulate material uniformly. This left a problem in the uniform formation of eutectic carbides.

Patent Document 3 proposes a method for producing a high carbon alloy steel free from coarse carbides. The technique described in Patent Document 3 contains C: 0.4 to 1.5%, and a high carbon alloy steel containing 1% or more in total of one or more selected from Cr, Mo, W and V This is a method for producing a high carbon alloy steel in which the molten metal is agitated under cooling to form a semi-solid slurry, which is then fed to a mold and cast. According to the technique described in Patent Document 3, by forming a solid-liquid mixed phase semi-solid slurry in which non-dendritic primary grains (ferrite) are suspended, a co-generation formed at the grain boundaries of the primary grains thereafter. It is said that coarsening of crystal carbide can be prevented. However, in the technique described in Patent Document 3, by refining the primary crystal γ, carbides crystallized in the remaining melt can be finely dispersed, and the solid solution / diffusion of carbon in the subsequent heat treatment can be promoted. The carbide cannot be deformed, and requires processing such as rolling and forging at a high temperature, resulting in an increase in manufacturing cost.
JP-A-2-55659 Japanese National Patent Publication No. 8-510298 JP 7-278727 A

  Apart from this, in order to further improve the wear resistance of the cast iron product, it is conceivable to add a large amount of V or the like to obtain a cast iron material in which a large amount of carbides such as VC are dispersed. Such cast iron material has the feature of crystallizing MC type carbides as primary crystals, and hard MC type carbides such as VC can be dispersed in a large amount, so that the wear resistance can be remarkably improved. Be expected. However, when such a cast iron material is cast in a sand mold, there is a problem that so-called gravity segregation due to levitation and settling of MC type carbide which is a primary crystal in the solidification process becomes remarkable. Further, when the amount of MC type carbide increases, the MC type carbide tends to be coarsened, and there is a problem that casting defects such as shrinkage cavities and porosity increase, and the toughness decreases.

  The present invention advantageously solves the above-mentioned problems of the prior art, reduces the occurrence of casting defects such as gravity segregation and shrinkage of MC type carbide, and makes it possible to easily and inexpensively cast iron products with excellent wear resistance. An object of the present invention is to provide a method for producing a wear-resistant cast iron product that can be produced.

  Among the above-mentioned problems, the present inventors firstly added V or Nb to form a hard carbide in addition to the composition of the cast iron product in addition to the high Cr-based cast iron composition in order to greatly improve the wear resistance. Attention was focused on a high-speed composition containing a large amount of W and W. In addition, for cast iron products with a high-speed composition, we have intensively studied various factors affecting the coarsening of MC-type carbides, the occurrence of casting defects such as shrinkage cavities, and the gravity segregation of carbides. As a result, primary MC type carbide is crystallized in the molten metal, the apparent viscosity of the molten metal is adjusted to an appropriate level, poured into a mold and solidified, specifically, the molten metal is preferably rapidly cooled, MC type carbide may be prepared by adjusting the casting temperature (temperature immediately before mold injection) T (° C.) within a predetermined temperature range, or stirring the molten metal at a temperature within the predetermined temperature range and then injecting it into a mold and solidifying it. It was found to be effective in reducing the segregation of gravity, preventing coarsening of MC type carbides, and reducing the formation of shrinkage cavities.

The present invention has been completed based on the above findings and further studies. That is, the gist of the present invention is as follows .

( 1 ) By mass%, C: 1.5 to 5.5%, Si: 1.5% or less, Mn: 1.2% or less, Cr: 4.0 to 20%, Mo: 2 to 12%, V: 3.0 to 20%, The temperature of T (° C.) immediately before casting the mold of the melt composed of the balance Fe and inevitable impurities is expressed by the following formula (1)
TA-0.5 (TA-TS) <T <TMC (1)
(Where T: temperature immediately before casting the mold (° C.), TA: crystallization start temperature of the austenite phase (° C.), TS: solidus temperature (° C.), TMC: temperature defined by the following equation (2) ( ℃),
TMC = 1170 + 64.5C + 24.6Si + 5.0Mn-11.1Cr-1.4Mo + 18.0V + 60.0Nb (2)
(Here, C, Si, Mn, Cr, Mo, V, Nb: content of each element (mass%)))
The method for producing a wear-resistant cast iron product is characterized in that after adjusting to satisfy the above, it is poured into a mold and solidified.

( 2 ) In ( 1 ), in adjusting the temperature of the molten metal immediately before casting the mold, the molten metal temperature is set to the TMC (° C) or higher, and then the molten metal is cooled at a cooling rate of 10 ° C / min or higher. The temperature is adjusted to the temperature T (° C.) immediately before the mold injection satisfying the expression (1).
( 3 ) In ( 1 ) or ( 2 ), the molten metal is agitated at a temperature satisfying the formula (1) before the pouring, and the method for producing a wear-resistant cast iron product.

( 4 ) In any one of (1) to ( 3 ), in addition to the above composition, in addition to mass, Ni: 5.5% or less, Co: 10.0% or less, Cu: 2.0% or less, W: 1.0% or less, Nb: 2.0% or less, Ti: 2.0% or less, Zr: 2.0% or less, B: A composition containing one or more selected from 0.1% or less Product manufacturing method.

  According to the present invention, there is no occurrence of casting defects such as shrinkage cavities, gravity segregation of carbides can be suppressed, hard MC type carbides can be finely dispersed, and cast iron products having excellent wear resistance are inexpensive and easy. It can be manufactured easily and has a remarkable industrial effect. Further, according to the present invention, there is an effect that it is possible to manufacture a thin cast iron product having excellent wear resistance. The cast iron product according to the present invention is suitable for wear resistant members such as jaw crushers, iron liners, and construction machines.

First, the reasons for limiting the composition of the molten metal used in the present invention will be described. Hereinafter, the mass% in the composition is simply expressed as%.
C: 1.5-5.5%
C is an essential element for forming a hard carbide that improves wear resistance. In the present invention, C is required to be contained in an amount of 1.5% or more. On the other hand, a large content exceeding 5.5% deteriorates toughness. For this reason, C was limited to the range of 1.5 to 5.5%. In addition, Preferably it is more than 1.5% and 4.5% or less, More preferably, it is 2.0 to 3.5%.

Si: 1.5% or less
Si is an element that acts as a deoxidizer and improves castability. It is desirable to contain 0.1% or more, but even if it exceeds 1.5%, the effect is saturated and an effect commensurate with the content is expected. Because it is not possible, it is economically disadvantageous. For this reason, Si was limited to 1.5% or less. In addition, Preferably it is 0.2 to 0.5%.

Mn: 1.2% or less
Mn is an element having the same action as Si, and it is desirable to contain 0.1% or more, but even if it exceeds 1.2%, the effect is saturated and an effect commensurate with the content cannot be expected, so economically It will be disadvantageous. For this reason, Mn was limited to 1.2% or less. In addition, Preferably it is 0.2 to 0.5%.
Cr: 4.0-20%
Cr is an important element that forms eutectic carbides, improves wear resistance, and dissolves in the matrix to strengthen the matrix structure and further improve corrosion resistance. Such an effect becomes remarkable when the content is 4.0% or more, but even if the content exceeds 20%, the effect is saturated, and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, Cr was limited to the range of 4.0 to 20%. In addition, Preferably it is 6 to 15%.

Mo: 2-12%
Mo, like Cr, is an element that forms carbides and effectively works to improve wear resistance, and has the effect of strengthening the carbides by solid solution in carbides. In the present invention, Mo is 2% or more. Containing is required. On the other hand, if the content exceeds 12%, the effect is saturated, and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, Mo was limited to the range of 2 to 12%. In addition, Preferably it is 3 to 7%.

V: 3.0-20%
V is an element that forms a hard MC type carbide and contributes to improvement of wear resistance. Such an effect becomes remarkable when the content is 3.0% or more. On the other hand, if the content exceeds 20%, the effect is saturated, and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, V was limited to the range of 3.0 to 20%. In addition, Preferably it is 4 to 15%.

In the present invention, the above composition is the basic composition of the molten metal. In addition to this basic composition, Ni: 5.5% or less, Cu: 2.0% or less, W: 1.0% or less, Co: One or more selected from 10.0% or less, Nb: 2.0% or less, Ti: 2.0% or less, Zr: 2.0% or less, B: 0.1% or less can be contained.
Ni, Cu, and W are all elements that have an action of strengthening the base structure, and can be selected from one or more as necessary.

Ni is an element that contributes to strengthening of the base structure through improvement of hardenability, and such an effect becomes remarkable when the content is 0.5% or more. On the other hand, if it exceeds 5.5%, an unstable structure such as an increase in the amount of retained austenite (γ) tends to be formed. For this reason, it is preferable to limit Ni to 5.5% or less.
Co is an element having an effect of stabilizing the structure at high temperature, and can be contained as necessary. The effect of Co becomes remarkable when the content is 0.1% or more. However, if the content exceeds 10.0%, the effect is saturated, and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, Co is preferably limited to 10.0% or less.

  Nb, like V, is an element that forms a hard MC-type carbide and has an effect of improving wear resistance, and can be contained if necessary. Such an effect of Nb becomes remarkable when the content is 0.2% or more. On the other hand, if the content exceeds 2.0%, the tendency of the carbides to become coarse increases, and there is a possibility that the desired improvement in wear resistance cannot be obtained. For this reason, it is preferable to limit Nb to 2.0% or less.

  Ti, Zr, and B are both elements that have the effect of suppressing the formation of coarse eutectic carbides and improving the wear resistance, and can be selected from one or more as required. Such an effect becomes remarkable when Ti: 0.01% or more, Zr: 0.01% or more, and B: 0.01% or more. On the other hand, if the content exceeds Ti: 2.0% and Zr: 2.0%, inclusions increase and the material becomes brittle, so the wear resistance is lowered. On the other hand, if the content exceeds B: 0.1%, segregation to the grain boundary becomes remarkable and the toughness decreases. For this reason, it is preferable to limit to Ti: 2.0% or less, Zr: 2.0% or less, and B: 0.1% or less, respectively.

In the present invention, in order to ensure the fluidity of the molten metal from the viewpoint of preventing casting defects, and in order to ensure the base hardness of a predetermined value or more from the viewpoint of improving the wear resistance, C, V, or further Within the above range of Nb content,
0.6 <{C-0.24V-0.13Nb} <2.0
(Here, C, V, Nb: content of each element (mass%))
It is preferable to adjust so as to satisfy the above. When Nb is not contained, the Nb term is calculated as zero.

The remainder of the molten metal other than the above components is Fe and inevitable impurities. As unavoidable impurities, P: 0.05% or less and S: 0.03% or less are acceptable.
In the present invention, the molten metal having the above composition is melted, poured into a predetermined mold (pouring), and solidified to obtain a cast iron product. The melting method of the molten metal is not particularly limited, and any known melting method can be applied.

In the present invention, the melt temperature immediately before pouring into the mold, that is, the temperature T (° C.) just before the mold pouring is expressed by the following equation (1).
TA-0.5 (TA-TS) <T <TMC (1)
(Where T: temperature immediately before casting the mold (° C.), TA: crystallization start temperature of γ phase (° C.), TS: solidus temperature (° C.), TMC: temperature defined by the formula (2) (° C. ))
Adjust to satisfy. Note that equation (2) is
TMC = 1170 + 64.5C + 24.6Si + 5.0Mn-11.1Cr-1.4Mo + 18.0V + 60.0Nb (2)
(Here, C, Si, Mn, Cr, Mo, V, Nb: content of each element (mass%))
It is.

In the molten metal composition used in the present invention, the carbide crystallized as the primary crystal is MC type carbide, and the TMC in the formula (1) causes the apparent viscosity of the molten metal to fall within the proper range by crystallizing the MC type carbide. It is assumed that the temperature is increased by using equation (2). It should be noted that elements not contained are calculated as zero.
TMC (℃) = 1170 + 64.5C + 24.6Si + 5.0Mn-11.1Cr-1.4Mo + 18.0V + 60.0Nb …… (2)
(Here, C, Si, Mn, Cr, Mo, V, Nb: content of each element (mass%))
Further, TA in the equation (1) is the crystallization start temperature (° C.) of the γ phase, and TS is the solidus temperature (° C.), which are calculated using the following equations, respectively. It should be noted that elements not contained are calculated as zero.

TA (° C) = 1055-61.5C-17.1Si-4.0Mn-0.7Cr-5.0Mo + 11.4Nb-4.0Ni
TS (° C) = 1099-12.7C + 0.4Si-6.5Mn-5.1Cr + 2.7Mo + 8.6V + 7.5Nb-4.3Ni
(Here, C, Si, Mn, Cr, Mo, V, Nb, Ni: content of each element (mass%))
By adjusting the temperature T (° C.) immediately before pouring the mold to a temperature that satisfies the formula (1), a large number of fine primary crystal carbides (MC type carbides) are crystallized in the melt before pouring. A state in which the viscosity has increased within the proper range is obtained, and the floating and settling of the MC type carbide, the primary crystal, that is, gravity segregation, is suppressed during the process of natural stirring and temperature drop during casting, and the carbide is uniform after solidification. A dispersed structure is obtained, wear resistance is improved, and a healthy cast iron product free from casting defects such as shrinkage cavities and microporosity accompanying the increase in the density of MC type carbide is obtained. On the other hand, if the formula (1) is not satisfied and the temperature T (° C) immediately before casting the mold is higher than TMC, the viscosity decreases due to the temperature rise of the unsolidified molten metal during the solidification process during casting. MC type carbides that crystallize in the vicinity of the solidification interface easily float and segregate MC type carbides. In addition, when the temperature T (° C.) immediately before casting the mold does not satisfy the formula (1), the fluidity of the molten metal is remarkably lowered due to the influence of the γ phase that grows in a dendritic form, and the microporosity and the shrinkage are reduced. Casting defects such as nests occur frequently. Therefore, in the present invention, the temperature T (° C.) immediately before casting the mold is adjusted to a temperature satisfying the expression (1) and poured into the casting mold.

As a preferable method for adjusting the temperature T (° C.) immediately before casting the mold to a temperature that satisfies the formula (1), a cooling plate or the like is provided in the runner (such as a tub or tundish) when the molten metal is poured. There are a method of quenching and quenching, a method of quenching by passing the molten metal through a water-cooled mold, a method of melting by adding a fine granular or plate-like cold material, etc., but the invention is limited to these is not.
When the molten metal is rapidly cooled, if the temperature of the molten metal has dropped below TMC (° C), the molten metal is once heated to a temperature of TMC (° C) or higher, and then the molten metal is heated to 10 ° C / min. It is preferable to cool to the temperature range satisfying the expression (1) at the above cooling rate. When the molten metal temperature is higher than TMC, it can be rapidly cooled at the above cooling rate without increasing the temperature. Thereby, the growth of the crystallized MC type carbide is suppressed, the fine MC type carbide is generated and dispersed, the gravity segregation of the MC type carbide is suppressed, and the occurrence of casting defects such as shrinkage can be prevented. In particular, this is effective when MC type carbide is easily coarsened and V is 8% or more. If the cooling rate is less than 10 ° C./min, MC type carbides may grow during cooling and become coarse. A more preferable range of the cooling rate is 50 ° C./min or more.

  In addition, when quenching to a temperature range below TA, which is the crystallization start temperature of the γ phase, in the temperature range satisfying the formula (1), the dendritic γ phase is refined in addition to the refinement of MC type carbides. Can be granulated. If the molten metal is cooled to a temperature of TA or lower without stirring, the viscosity of the molten metal increases rapidly and the castability tends to decrease. For this reason, when cooling a molten metal to the temperature below TA, it is preferable to use stirring together. By using agitation together, the occurrence of casting defects can be suppressed.

  Moreover, before pouring into a casting_mold | template, it is preferable to stir a molten metal at the temperature of the range which satisfies Formula (1). By stirring the molten metal at a temperature satisfying the formula (1), the MC type carbide is easily granulated, thereby further improving castability and toughness. As the stirring method, any known stirring method such as mechanical stirring by an impeller, stirring by gas bubbling, or stirring using electromagnetic force can be applied.

The mold used is preferably a mold. By using a mold having a high cooling rate, the solidification rate is accelerated, and further miniaturization of MC type carbide, eutectic carbide, and the like are possible.
The cast iron product obtained by the above manufacturing method is reheated to an appropriate temperature (for example, a solid-liquid coexistence region) and then subjected to processing such as compression, so that a liquid phase containing a large amount of eutectic carbides oozes out on the surface layer. It is easy to come out, and the surface layer becomes a layer in which the carbide phase is concentrated, while the inner layer becomes a layer having little carbide phase and rich in toughness, and a cast iron product having a gradient function can be obtained.

The cast iron product obtained by the above manufacturing method has substantially the same composition as the above-described molten metal composition, and further, granular MC type carbide having a particle size of 5 to 30 μm is dispersed in the matrix in an area ratio of 5 to 30%. It becomes a cast iron product having a structure. By setting it as such a structure | tissue, abrasion resistance, grindability, toughness, etc. improve notably.
Any of the cast iron products manufactured by the above-described manufacturing method may be subjected to a tempering treatment as necessary in order to adjust to a desired hardness. As the tempering treatment, after austenitizing, quenching treatment is performed by quenching to a temperature below the bainite transformation start temperature to a temperature above the martensite transformation start temperature, and then holding or gradually cooling to form a bainite texture in the base structure. It is preferable to perform a process of performing a tempering process for adjusting to a predetermined appropriate hardness.

  After the molten metal having the composition shown in Table 1 is melted in an electric furnace, the molten metal temperature is adjusted to the temperature immediately before casting the mold shown in Table 2, then poured into a self-hardening mold using dredged sand, solidified, and cast iron product. (Weight: 30 kg, size: 60 mmφ × 150 mm height). The cast iron product was then tempered at a quenching temperature of 1000 ° C and a tempering temperature of 500 ° C. In some cases, immediately before pouring, a bowl with a cooling plate was installed in the pouring part to perform rapid cooling and / or stirring with an impeller.

Each temperature of TMA, TA, and TS in Table 1 is a value calculated using the above formula.
The resulting cast iron product was subjected to appearance and cross-section observation tests, hardness tests, and wear resistance tests. The test method was as follows.
(1) Appearance and cross-sectional observation inspection About the obtained cast iron product, surface defects such as shrinkage cavities and the like, and a central longitudinal section sample of the obtained cast iron product are collected, and the central longitudinal section sample is entirely polished. Then, the presence or absence of casting defects such as shrinkage cavities and porosity, and the presence or absence of gravity segregation of MC type carbide were examined visually and with an optical microscope (100 times). The case where there was no such casting defect was marked with ◯, the case where these casting defects were minor and could be recognized by an optical microscope, and the case where a large amount of these casting defects were present and could be visually confirmed were marked with x. Further, the case where gravity segregation of MC type carbide was present was evaluated as x, and the case where there was not gravity was evaluated as ◯.

(2) Hardness test About the central longitudinal cross-section sample extract | collected from the obtained cast iron article, hardness Hs was measured using the Shiore hardness meter. The measurement position is the center in the height direction of the cast iron product. Measure 10 points in total, 0, 5, 10, 15, 20mm from both surfaces (both sides) in the center direction, and calculate the arithmetic average of the cast iron. The hardness of the product.

(3) Abrasion resistance test A 10mmφ × 50mm length round bar-shaped test piece was cut out from the vicinity of the surface of the central part in the height direction of the center longitudinal section sample taken from the obtained cast iron product, and a rotary wear test was performed. . The rotary wear test is a test in which the test piece is subjected to rotary wear (rotation speed: 640 rpm, test piece speed: 10 m / s) in a mud mixed with silica sand, silica and water, and the test time is 20 hours. The wear loss of the test pieces was measured and the wear resistance was evaluated. The wear resistance was expressed as a ratio (wear loss of the test material / wear loss of the conventional example) to the wear loss of the conventional example based on the wear loss of the high Cr cast iron (conventional example) (1.00). The smaller the wear resistance ratio, the better the wear resistance. Note that the wear resistance test was not performed on the comparative example in which the castability deteriorated. The obtained results are shown in Table 3.

本発明例はいずれも、鋳造欠陥もなく、MC型炭化物の重力偏析もなく、従来例に比べて耐摩耗性に優れた鋳鉄品となっている。一方、本発明の範囲を外れる比較例は鋳造欠陥が発生しているか、あるいはMC型炭化物の重力偏析が発生しているか、耐摩耗性が劣化している。

In all of the examples of the present invention, there is no casting defect, gravity segregation of MC type carbides, and cast iron products having superior wear resistance as compared with the conventional examples. On the other hand, in comparative examples that are out of the scope of the present invention, casting defects have occurred, gravity segregation of MC type carbides has occurred, or wear resistance has deteriorated.

Claims (4)

% By mass
C: 1.5 to 5.5%, Si: 1.5% or less,
Mn: 1.2% or less, Cr: 4.0-20%,
Mo: 2-12%, V: 3.0-20%
The molten metal having a composition comprising the balance Fe and inevitable impurities is adjusted so that the temperature T (° C.) immediately before the mold injection satisfies the following formula (1), and then injected into the mold and solidified. A method for producing a wear-resistant cast iron product.
Record
TA-0.5 (TA-TS) <T <TMC (1)
Where T: temperature immediately before mold injection (° C.),
TA: Austenite phase crystallization start temperature (° C),
TS: Solidus temperature (° C),
TMC: Temperature (° C) defined by the following equation (2)
TMC = 1170 + 64.5C + 24.6Si + 5.0Mn-11.1Cr-1.4Mo + 18.0V + 60.0Nb (2)
(Here, C, Si, Mn, Cr, Mo, V, Nb: content of each element (mass%)) In adjusting the temperature of the molten metal immediately before mold injection, the molten metal temperature is set to the TMC (° C) or higher, and then the molten metal is cooled at a cooling rate of 10 ° C / min or higher. 2. The method for producing a wear-resistant cast iron product according to claim 1 , wherein the temperature is adjusted to a temperature T (° C.) immediately before the mold injection that satisfies the requirement. The method for producing a wear-resistant cast iron product according to claim 1 or 2 , wherein the molten metal is stirred at a temperature satisfying the formula (1) before the injection.   In addition to the above composition, Ni: 5.5% or less, Co: 10.0% or less, Cu: 2.0% or less, W: 1.0% or less, Nb: 2.0% or less, Ti: 2.0% or less, Zr: 2.0 % Or less, B: It is set as the composition containing 1 type, or 2 or more types chosen from 0.1% or less, The manufacturing method of the wear-resistant cast iron product in any one of Claim 1 thru | or 3 characterized by the above-mentioned. .