JP2001247905A - Heat resistant and wear resistant composite structural member and its producing method - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a heat resistant and wear resistant composite structural member used for the one to be subjected to temperature and loads such as a guide roll and a roll for rolling used at a rolling factory in an iron making field and to provide its producing method. SOLUTION: In this heat resistant and wear resistant composite structural member, powder having a componential composition containing, by mass, 0.9 to 2.5% C, 0.15 to 1.5% Si, 0.1 to 2.0% Mn, 3.5 to 12.0% Cr, 3.0 to 10.0% Mo, 0.8 to 8.0% V and 1.0 to 10.0% W, furthermore containing one or more kinds selected from 0.5 to 3.0% Ni, 0.8 to 8.0% Nb and 1.0 to 12.0% Co, and the balance Fe with inevitable impurities is formed on the outside of a base metal composed of carbon steel as a first HIP treated layer, and, on the outer layer of the first HIP treated layer, a second HIP treated layer composed of a powdery mixture consisting of the powder of one or more kinds among metallic carbide, nitride, oxide and boride of 5 to 30% by total volume ratio and the balance powder of above components is formed. Moreover, the producing method uses the same.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a heat-resistant and wear-resistant composite structural member used for a member subjected to a temperature or a load such as a guide roll and a roll for rolling used in a rolling mill in the field of steelmaking. The present invention relates to the manufacturing method.

[0002]

2. Description of the Related Art In recent years, in the field of steel rolling, for example, in a rolling mill or the like, there is a high demand for improving the accuracy, quality and productivity of products, and therefore operating conditions are severe. Therefore,
Durability is required for guide rolls and rolling rolls, which are one of the tools used to manufacture the above products. Particularly, the reliability of strength is secured mainly because of the reduction in tool unit consumption and maintenance. There is a strong demand for improved heat resistance and wear resistance. On the other hand, regarding the improvement of heat resistance and wear resistance,
Many researches and developments have been attempted so far, and as one of the latest technologies, for example, as disclosed in Japanese Patent Laid-Open No. , One of metal carbides, nitrides and borides
It has a two-layer structure in which a second processing layer is formed by performing HIP processing on a composite powder composed of a powder composed of at least one kind and a high-speed steel (high-speed steel) powder, and a hardening heat treatment is performed on the outer layer.

[0003]

SUMMARY OF THE INVENTION The above-mentioned Japanese Patent Application Laid-Open No. 10-2
The technology disclosed in Japanese Patent No. 80101 has a two-layer structure of high-speed cermet (composite powder of a metal compound and high-speed steel) having excellent heat and abrasion resistance in the outer layer and tough carbon steel in the inner layer. Therefore, it has both heat and abrasion resistance and strength reliability at the same time. However, since the outer HSS cermet is diffusion-bonded to the inner carbon steel and is subjected to hardening heat treatment, the outer layer expands due to martensitic transformation during this hardening heat treatment, and the boundary between the inner and outer layers after the hardening heat treatment. , The tensile residual stress in the radial direction peaks.

On the other hand, the bonding strength at the boundary decreases as the proportion of ceramic added to the high-speed cermet of the outer layer or the carbon content of the high-speed steel increases. If the bonding strength is reduced, there is a risk that cracks may occur at the boundary during manufacturing or use. Therefore, in the technology disclosed in Japanese Patent Application Laid-Open No. 10-280101, in which high-speed cermet is diffusion-bonded to the outside of carbon steel, the outer layer material is required to secure the bonding strength at the boundary at the bonding portion. Increase the carbon content of ceramics and high speed steel in high speed cermet,
Moreover, it is difficult to increase the bonding strength at the boundary. For this reason, there is a problem that it is difficult to give sufficient strength to the boundary portion with the two-layer structure material disclosed in Japanese Patent Application Laid-Open No. 10-280101.

[0005]

SUMMARY OF THE INVENTION The present invention solves the above-mentioned problems and has the functions and effects of heat resistance and abrasion resistance of the prior art and has excellent adhesive strength to a base material. It is an object of the present invention to provide a heat-resistant and abrasion-resistant composite material having high strength reliability and a wide range of practical applications. The gist of the invention is as follows: (1) In the outside of a base material made of carbon steel, C:
0.9-2.5%, Si: 0.15-1.5%, Mn:
0.1 to 2.0%, Cr: 3.5 to 12.0%, Mo:
3.0 to 10.0%, V: 0.8 to 8.0%, W: 1.
A powder having a component composition of 0 to 10.0%, with the balance being Fe and unavoidable impurities, forms a first HIP-treated layer.
In the outer layer of the HIP treatment layer, a powder composed of one or more of carbides, nitrides, oxides, and borides of metal in a total volume ratio of 5 to 30%, and a balance composed of a powder composed of the above components A heat- and wear-resistant composite structural member, wherein a second HIP treatment layer made of a mixed powder of the above is formed.

(2) In addition to the components described in (1) above,
i: 0.5 to 3.0%, Nb: 0.8 to 8.0%, C
o: A heat- and wear-resistant composite structural member characterized in that one or more of 1.0 to 12.0% of the same are contained. (3) A heat- and wear-resistant composite structural member, wherein the first treatment layer according to (1) or (2) is formed by thermal spraying or overlay welding.

(4) A first step of forming a pre-alloyed composite powder of the mixed powder for the second HIP processing layer according to the above (1) by a mechanical alloying method, and thereafter,
(1) or (2) above the base material made of carbon steel
A second step of filling the powder described above for the first layer, and filling the outside of the powder for the first layer with the previously prepared composite powder for the second HIP treatment, and thereafter, at a temperature of 1000 to 12
HIP at 00 ° C., pressure 98-196 MPa, 2-5 hours
A method for producing a heat- and wear-resistant composite structural member, comprising: a third step of performing a treatment to form a three-layer structure; and a fourth step of performing a curing heat treatment on the structural material.

(5) A first step of forming a pre-alloyed composite powder of the mixed powder for the second HIP processing layer according to the above (1) by a mechanical alloying method, and thereafter,
(1) or (2) above the base material made of carbon steel
A first layer is formed by spraying or overlay welding the powder described above, and the second HIP prepared in advance is formed outside the first layer.
A second step of filling the composite powder for processing, followed by a temperature of 1000-1200 ° C., a pressure of 98-196 MPa,
A method for producing a heat- and wear-resistant composite structural member, comprising: a third step of performing a HIP treatment for up to 5 hours to form a three-layer structure; and a fourth step of curing and heat-treating the structural material.

[0009]

DESCRIPTION OF THE PREFERRED EMBODIMENTS Hereinafter, the reasons for limiting the component compositions applied to the first and second layers according to the present invention will be described. C: 0.9 to 2.5% C mainly forms a martensite phase which is dissolved in the matrix. Further, Fe, Cr, Mo, N
Combines with b, V, W, etc. to form various carbides. However, if it is less than 0.9%, the amount of the carbide is small, and the wear resistance cannot be obtained. On the other hand, if it exceeds 2.5%, coarse carbides are formed, which causes a decrease in toughness and a rough skin. Therefore, the range is set to 0.9 to 2.5%.

Si: 0.15 to 1.5% Si is added for the purpose of deoxidizing. However, 0.1
If it is less than 5%, the effect is insufficient, and if it exceeds 1.5%, the toughness is reduced.
To 1.5%. Mn: 0.1 to 2.0% Mn is added for the purpose of enhancing the deoxidizing and desulfurizing actions and the hardenability and increasing the matrix hardness. However, if it is less than 0.1%, the effect is insufficient, and if it exceeds 2%, the toughness is reduced. Therefore, the range is set to 0.1 to 2.0%.

Cr: 3.5 to 12.0% Cr forms a solid solution in the matrix to enhance quenchability and form carbides combined with C. However, 3.5
%, The amount of carbides is small, and the wear resistance is reduced. If it exceeds 12.0%, coarse carbides are formed,
This leads to a decrease in toughness. Therefore, the range is set to 3.5 to 12.
0%. Mo: 3.0 to 10.0% Mo, like Cr, forms a solid solution in the matrix to strengthen the matrix and combines with C to form a carbide. In order to strengthen the base, the content must be at least 3.0% or more, but even if it exceeds 10.0%, the effect does not change.
The upper limit was set to 10.0% for economic reasons.

V: 0.8-8.0% V combines with C to form a high hardness MC carbide. However, if the content is less than 0.8%, the effect is insufficient, and 8.0% is used.
%, It is not preferable because the amount of dissolved carbon in the matrix decreases and the hardness of the matrix decreases. Therefore, the range was set to 0.8 to 8.0%. W: 1.0 to 10.0% W, like Mo, is solid-dissolved in the matrix to strengthen the matrix and to form carbides combined with C. In order to strengthen the matrix, the content must be at least 1.0% or more. However, if it exceeds 10.0%, coarse carbides are formed and the toughness is reduced. Therefore, the range is set to 1.0 to 10.
0%.

The basic components of the material of the present invention are as described above. However, depending on the required properties required for the composite structural material to which the present invention is applied, other components, in addition to the above-mentioned chemical components of the present invention, Further, the following components may be contained. Ni: 0.5 to 3.0% Ni is dissolved in the matrix to stabilize austenite of the matrix and improve quenchability. For this reason, when a large size member is manufactured, a small amount may be contained. However, if the content exceeds 3.0%, austenite is excessively stabilized, austenite remains, and it becomes difficult to secure hardness. During hot rolling, deformation may occur. However, less than 0.5% has no effect. Therefore, the range was set to 0.5 to 3.0%.

Nb: 0.8-8.0% Nb is an important element that combines with C to form MC carbide which greatly contributes to wear resistance. However, if it is less than 0.8%, the amount of carbides is insufficient, so that the wear resistance cannot be secured, and
% Leads to a decrease in toughness. In particular, it is added when a marked improvement in wear resistance is required. Therefore,
The range is set to 0.8 to 8.0%. Co: 1.0 to 12.0% Most of Co is dissolved in the matrix to strengthen the matrix. Therefore, it has the effect of improving the hardness and strength at high temperatures. However, if it is less than 1.0%, the effect is insufficient, and if it exceeds 12.0%, the effect is saturated. Therefore, from the viewpoint of economy, 12.0% or less is desirable. In particular, when the surface temperature becomes high, for example, 600 ° C. or higher, and the high-temperature abrasion resistance of the surface is improved, it may be added.

Next, the reason why the total mixing ratio of one or more ceramics (metal carbides, nitrides, oxides, borides) is 5 to 30% by volume is that the hard particles are hardened as the mixing ratio increases. However, if the content is less than 5%, the effect is small, and if it exceeds 30%, defects due to a decrease in the strength of the outer layer, surface roughening, and the like are liable to occur, which is not preferable. In mechanical alloying, a mixed powder of ceramics and powder is repeatedly crushed and fixed to form a finely dispersed composite powder structure, thereby improving heat resistance, wear resistance, and surface roughness.

On the other hand, if the HIP temperature is lower than 1000 ° C., the sintering is not efficient, and pore defects tend to remain. If the temperature exceeds 1200 ° C., the particles are coarsened and the strength is reduced. In addition, the pressure is 98
If the pressure is at least MPa, the pores can be eliminated. However, 196
The effect is the same even when the pressure exceeds MPa, and the upper limit is set to 196 MPa in consideration of economy and pressure resistance of equipment.

Hereinafter, the present invention will be described in detail with reference to the drawings. Table 1 shows the chemical composition of the first layer powder according to the present invention. In addition, titanium carbide (TiC) is used as a typical example of the metal carbide as the powder for the second layer, and the powder having the chemical composition shown in Table 1 has a volume fraction of 20%.
Was added to form a mixed powder. Thereafter, the mixture is
An alloying operation is performed for 60 hours by a mechanical alloying method using a UJ2 ball to produce a mixed powder.

[0018]

[Table 1]

As a test filling container, the one shown in FIG. 1 is used. That is, FIG. 1 is a diagram showing a capsule structure for preparing a boundary strength measurement test piece. As shown in FIG. 1, FIG. 1A shows a three-layer structure according to the present invention, and FIG. 1B shows a conventional two-layer structure. The capsule 1, which is the container body, is made of carbon steel and has an inner diameter D
Was 14.2 mmφ and the height H was 140 mm. All the base materials 4 used solid cylinders of SCM material and were installed at the bottom of the capsule 1. 2 shown in FIG.
The layer structure test piece is in contact with the base material 4 and is filled with the powder 3 for the second layer, and the three-layer structure test material of the present invention shown in FIG.
And the first layer powder 2 was filled to a thickness of about 5 mm, and the second layer powder 3 was filled thereon.

After the above filling, vacuum deaeration, 1140 ° C.
After HIP treatment at 147 MPa for 3 hours, and after softening and annealing, quenching was performed at 1000 ° C. × 2 hours, cooled to room temperature, and then tempered three times at 550 ° C. × 3.5 hours. Thereafter, a test piece of １ ／ size of a JIS No. 4 tensile test piece with the boundary between the base material 4 of each test material and the first layer powder 2 as a center was sampled, and its mechanical strength was measured. Table 2 shows the results. As a result, as shown in Table 2, it is understood that the material of the present invention has higher tensile strength, elongation, and reduced drawing compared to the conventional two-layer structure.

[0021]

[Table 2]

FIG. 2 is a diagram showing the state of fracture at the boundary of a tensile test piece. In the case of the conventional two-layer structure shown in FIG. 2B, the cut portion breaks at the boundary between the base material 4 and the steel composed of the powder 3 for the second layer, whereas FIG. The present invention material shown in FIG. 1 is firmly joined to any of the boundaries between the steel composed of the base material 4 and the first layer powder 2 and the steel composed of the second layer powder 3, and the fracture position is the base material having high toughness. It is broken by. This also indicates that the strength of the boundary portion of the material of the present invention is extremely high.

As for the stress state of the composite roll for rolling, the load stress and the thermal stress of the rolling are added to the residual stress of the roll generated at the time of manufacturing. FIG. 3 shows such a stress state. That is, FIG. 3 is a diagram showing the residual stress distribution in the radial direction of the roll cross section. FIG. 3A shows the residual stress distribution in the three-layer structure of the present invention, and FIG. 3B shows the residual stress distribution in the conventional two-layer structure.
In the quenching, since the second layer expands by martensitic transformation due to quenching, the tensile residual stress peaks at the boundary with the base material, so if the boundary strength is not sufficient, during quenching, during machining or during rolling use Cracks may occur at the boundaries. In the case of the three-layer structure of the present invention, as shown in FIG. 3A, the peak of the tensile residual stress is at the boundary between the base material and the first layer. That is, in the case of the material of the present invention, it is understood that the boundary is a composite material having higher tensile strength at the boundary than the tough base material and having high reliability against crack generation from the boundary.

Hereinafter, the present invention will be described specifically with reference to examples.

EXAMPLES (Example 1) For the powder of the first layer, see Table 3
The two types of powder having the chemical composition shown in Table 1 were used.
As the powder of the second layer, titanium carbide was prepared, and the two kinds of powders in Table 3 were mixed at a volume ratio of 10% and 20%, respectively, to prepare a total of four kinds of mixed powders. Thereafter, the four types of mixed powders were alloyed for 60 hours by a mechanical alloying method using SUJ2 balls to produce composite powders. On the other hand, the filling container is
In order to prepare a wear test piece of × 10 mmt, FIG.
Four conventional two-layered capsules shown in FIG. 4B and two three-layered capsules of the present invention shown in FIG. 4A were prepared. They are,
The inner diameter is 78 mm, the height is 60 mm, and two test pieces can be collected from one capsule. Filling is 50m in the center of capsule
A low-alloy carbon steel base material of mφ was set, and in the conventional two-layer structure, four kinds of second-layer powders were filled one by one around the periphery to make a total of four pieces.

[0025]

[Table 3]

FIG. 5 is a view showing a filling step of the three-layered capsule according to the present invention. That is, in the three-layer structure of the present invention, as shown in FIG. 5 (a), the base material 4 is set at the center of the capsule 1, and the first layer and the second layer are provided between the capsule 1 and the base material 4. The partition cylinder 5 is set in order to form a space. In such a state, as shown in FIG. 5 (b), the first layer space is filled with the first layer powder, the second layer space is filled with the second layer powder, and the partition cylinder 5 is raised. Fill both powders to the top. Thereafter, as shown in FIG. 5 (c), the partition wall cylinder 5 is removed from the base material 4 held by the pedestal jig 7 by the pull-up screw 6, the upper capsule 8 is welded, and after degassing, it is sealed. A second layer in which the first layer powder (high-speed powder) is formed to a thickness of about 2 to 3 mm around the outer periphery of the base material, and 2.3% C high-speed steel is mixed with 10% and 20% of TiC is formed in the above procedure. Layer powder (MA high-speed cermet composite powder) was filled, and two powders each were prepared.

After the above filling, after vacuum degassing, 1140
C., 147 MPa, HIP treatment for 3 hours, and roughening was performed after softening annealing. After quenching, it was cooled to room temperature at 1000 ° C. × 2 hours, and then tempered three times at 550 ° C. × 3.5 hours, followed by finishing. Table 4 shows the production results. In the conventional two-layer structure material, cracks may occur at the composite boundary during quenching or machining, and the T
Boundary cracks tend to occur easily in a material having a two-layer structure of a MA high-speed cermet having a high iC content. On the other hand, in the three-structure material of the present invention, no boundary crack was generated even in MA high-speed cermet having a high content of TiC and high carbon. Note that the set thickness of the first layer is 0.2
~ 20 mm is preferred. If it is less than 0.2 mm, the effect is small, and if it exceeds 20 mm, the effect is saturated.

[0028]

[Table 4]

(Example 2) As the powder of the first layer, those having the chemical composition of the powder shown in Table 5 were used. Also,
For the powder of the second layer, titanium carbide was prepared and mixed with the powders in Table 5 at a volume ratio of 10% to prepare a mixed powder. Thereafter, an alloying operation was performed for 40 hours by a mechanical alloying method using SUJ2 balls to produce a composite powder. On the other hand, the filling container has an inner diameter of 93 mm and a height of 190 mm as shown in FIG.
Two products of (b) can be collected. For filling, a 45 mmφ low alloy carbon steel base material (SCM440) was set in the center of the capsule, and the first layer powder 2 was formed to a thickness of about 3 to 4 mm around the base material as shown in FIG. 10% TiC in powder
% Mixed powder 3 was filled to prepare a filler having a three-layer structure. After the above filling, after vacuum deaeration, 1140 ° C,
HIP treatment was performed at 147 MPa for 3 hours, and roughening was performed after softening annealing. After quenching, the specimen was cooled to room temperature at 1140 ° C. for 0.5 hour, tempered three times at 550 ° C. for 3.5 hours, and then 74 mm in diameter and 7 mm in length as shown in FIG.
Finishing was performed on a 0 mm wire rod guide roll. No trouble of boundary crack occurred during manufacturing, and it could be used smoothly.

[0030]

[Table 5]

(Example 3) As the powder of the first layer, the powder having the chemical composition shown in Table 6 was used. Also,
For the powder of the second layer, titanium carbide was prepared and mixed with the powder in Table 6 at a volume ratio of 10% to prepare a mixed powder. Thereafter, an alloying operation was performed for 40 hours by a mechanical alloying method using SUJ2 balls to produce a composite powder. On the other hand, the filling container has an inner diameter of 387 mm and a height of 263 mm as shown in FIG.
Two products of (b) can be collected. Filling is performed by setting a low alloy carbon steel base material of 215 mmφ in the center of the capsule and, as shown in FIG.
And a second mixture of 10% TiC and the powder shown in Table 6
The layer powder 3 was filled to prepare a three-layer filler. After the above filling, after vacuum deaeration, 1140 ° C, 147 MPa,
HIP treatment was performed for 3 hours, and roughening was performed after softening annealing. After quenching, cooling to normal temperature at 1140 ° C. × 0.5 hour, and tempering three times at 550 ° C. × 3.5 hours, FIG.
As shown in (b), a large diameter intermediate work roll for rolling a wire having a diameter of 330 mm and a length of 95 mm was finished. There was no trouble of boundary cracking during production, and it could be used smoothly.

[0032]

[Table 6]

(Example 4) As the powder of the first layer, the one having the chemical composition of the powder for thermal spraying shown in Table 7 was used.
Further, as the powder of the second layer, titanium carbide was prepared and mixed with a high speed steel for MA high speed cermet in Table 7 at a volume ratio of 10% to prepare a mixed powder. Thereafter, alloying was performed for 72 hours by a mechanical alloying method using SUJ2 balls to produce a composite powder. On the other hand, filling containers
80 mm in inner diameter and 120 mm in height as shown in FIG.
Thus, two products shown in FIG. 8B can be collected from one capsule. Filling is about 0.5 mm for the first layer powder on the surface of a low alloy carbon steel base material of 45 mmφ caliber shape in the center of the capsule.
Set the material sprayed by the reduced pressure plasma method to the thickness,
A second layer of 20% TiC mixed with the powder for the second layer on the outer periphery thereof
Layer powder (MA high speed cermet composite powder)
A layered packing material was prepared.

[0034]

[Table 7]

After the above filling, after vacuum degassing, 1140
C., 147 MPa, HIP treatment for 3 hours, and roughening was performed after softening annealing. The quenching is performed by cooling to room temperature at 1140 ° C. × 0.5 hours, and then tempering three times at 550 ° C. × 3.5 hours, and then for rolling a wire rod having a diameter of 60 mm and a length of 40 mm as shown in FIG. Finish processing was performed on the guide roll. Table 8 shows that there were no problems such as cracks during production.
As shown in Fig. 5, the durability was 10 times or more that of the conventional tool roll. The method of spraying or overlay welding on the base material shown in the present embodiment is difficult to implement by the method of filling ceramic powder using a partition cylinder as in the above-described embodiment because the base material has a deep caliber, for example. This is an effective method in such cases. In this case, the thickness at the time of thermal spraying and overlaying on the base material is preferably 0.1 to 1.0 mm. If it is less than 0.1 mm, the effect is not obtained, and if it exceeds 1.0 mm, it is not economical.

[0036]

[Table 8]

In the embodiments described above, the application examples of the present invention are guide rolls and intermediate work rolls for wire rod rolling. However, the application examples are not limited to these. For example, other hot and cold rolling may be used. It can be widely applied to rolls, tools and the like, and in the examples, the material of the base material is a low alloy carbon steel (SCM440) from carbon steel. Is not limited to this, and may be any carbon steel, and can be widely applied, for example, carbon steel for machine structures, bearing steel, and the like. In this case, when selecting the base material, it may be appropriately selected from the toughness, hardness and the like required for the composite structural material.

[0038]

As described above, according to the present invention, the heat-resistant and abrasion-resistant properties of the prior art, the excellent adhesion strength to the base material, the high strength reliability, and the extremely practical range of application can be obtained. This is an excellent effect that can provide a wide heat- and wear-resistant composite material.

[Brief description of the drawings]

FIG. 1 is a diagram showing a capsule structure for producing a boundary strength measurement test piece,

FIG. 2 is a diagram showing the state of fracture at the boundary of a tensile test piece;

FIG. 3 is a diagram showing a residual stress distribution in a radial direction of a roll cross section;

FIG. 4 is a diagram showing a capsule and a powder filling state;

FIG. 5 is a view showing a filling step of a three-layered capsule according to the present invention;

FIG. 6 is a diagram showing a three-layer structure capsule for a guide roll for wire rod rolling and its product,

FIG. 7 is a view showing a three-layer structure capsule for an intermediate work roll for wire rod rolling and a product thereof;

FIG. 8 is a view showing a three-layered capsule for a guide roll for wire rolling in which a base material is formed into a caliber and a product thereof.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 Capsule 2 Powder for 1st layer 3 Powder for 2nd layer 4 Base material 5 Partition cylinder 6 Pulling screw 7 Pedestal jig 8 Upper capsule

Continued on the front page (51) Int.Cl. ⁷ Identification symbol FI Theme coat II (reference) C22C 38/38 C22C 38/38 38/58 38/58 C23C 4/06 C23C 4/06 // C22C 33/02 C22C 33 / 02 B (72) Inventor Masatoshi Ayagaki 46-59 Nakahara, Tobata-ku, Kitakyushu-shi, Fukuoka F-term in the Engineering Business Unit of Nippon Steel Corporation 4E016 CA06 CA08 CA09 CA10 DA03 EA08 EA16 EA22 4K018 AA34 AA36 AB01 AB02 AB03 AB04 AC01 BA11 BA16 BC16 EA11 JA27 KA17 4K031 AA02 AB02 AB08 CB11 CB22 CB23 CB24 CB26 CB28 DA04 FA07

Claims (5)

[Claims] 1. The method according to claim 1, wherein a mass%
C: 0.9 to 2.5%, Si: 0.15 to 1.5%, Mn: 0.1 to 2.0%, Cr: 3.5 to 12.0%, Mo: 3. 0 to 10.0%, V: 0.8 to 8.0%, W: 1.0 to 10.0% A powder having a component composition comprising the balance of Fe and unavoidable impurities is used as a first HIP treatment layer. In the outer layer of the first HIP treatment layer, a powder composed of one or more of metal carbides, nitrides, oxides, and borides is added in a total volume ratio of 5%.
A heat- and abrasion-resistant composite structural member, wherein a second HIP-treated layer made of a mixed powder with a powder containing the above components is formed in an amount of up to 30%. 2. The composition according to claim 1, further comprising: Ni: 0.5 to 3.0%, Nb: 0.8 to 8.0%, Co: 1.0 to 12.0%. A heat- and wear-resistant composite structural member characterized by containing one or more kinds. 3. A heat- and wear-resistant composite structural member, wherein the first treatment layer according to claim 1 or 2 is formed by thermal spraying or overlay welding. 4. A first step of forming a composite powder in which the mixed powder for the second HIP processing layer according to claim 1 is alloyed in advance by a mechanical alloying method, and thereafter, a base material made of carbon steel 3. A second step of filling the powder according to claim 1 or 2 for the first layer outside the powder, and filling the composite powder for the second HIP processing prepared in advance outside the powder for the first layer. After that, a HIP treatment is performed at a temperature of 1000 to 1200 ° C., a pressure of 98 to 196 MPa, and 2 to 5 hours.
A method for producing a heat- and wear-resistant composite structural member, comprising: a third step of forming a layered structure; and a fourth step of curing and heat-treating the structural material. 5. A first step of forming a pre-alloyed composite powder of the mixed powder for the second HIP processing layer according to claim 1 by a mechanical alloying method, and thereafter, a base material made of carbon steel A first layer is formed on the outside of the first layer by thermal spraying or overlay welding of the powder according to claim 1 or 2, and the outside of the first layer is filled with the previously prepared composite powder for the second HIP processing. A second step, followed by a temperature of 1000 to 1
200 ° C., pressure 98-196 MPa, HI for 2-5 hours
A method for producing a heat- and wear-resistant composite structural member, comprising: a third step of performing a P treatment to form a three-layer structure; and a fourth step of curing and heat-treating the structural material.