JPH07166291A - Production of graphite-containing high speed steel type composite rotary member - Google Patents

Abstract

PURPOSE:To obtain composite rolls and composite rollers, excellent in wear resistance and surface roughing resistance, by casting an outer layer consisting of high speed steel type material on the outside peripheral surface of a shaft member by a method of continuous cladding by welding (casting). CONSTITUTION:A shaft member, made of tough material, of a cylindrical mold is continuously allowed to descend concentrically. At that time, a molten outer layer material is continuously poured into the space between the mold and the shaft material and solidified in the bottom of the mold, and the outer layer is integrally joined to the outside peripheral surface of the shaft material, by which a composite rotary member can be formed. As this outer layer material, a high speed steel type material, having a composition consisting of 1.8-3.6% C, 1.0-3.5% Si, 0.1-2.0% Mn, 0.5-10.0% Ni, 2.0-10% Cr, 0.1-10% Mo, 0.1-10% W, 1.5-10%, in total, of V and/or Nb, and the balance essentially Fe, is used. As the shaft member, it is preferable to use high grade cast iron, ductile cast iron, or graphite steel, having low Young's modulus and excellent in toughness and thermal conductivity.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a rotary member such as a composite roll or a composite roller in which an outer layer made of a high speed cast iron material is cast and formed on the outer peripheral surface of a shaft member by a so-called continuous overlay welding method. .

[0002]

2. Description of the Related Art A suitable method for producing a composite roll in which an outer layer, which is a layer used for rolling, is welded and integrated on the outer peripheral surface of a shaft member made of a tough material is disclosed in JP-A-60-180660. As described above, there is a so-called continuous overlay welding (casting) method. This method is equipped with a high-frequency induction heating coil in the upper part, and a shaft member made of a tough material is continuously and concentrically lowered into a cylindrical continuous build-up mold equipped with a water-cooled mold in the lower part. The molten outer layer material is continuously injected into the gap between the mold and the shaft member and solidified at the bottom of the mold,
In this method, an outer layer is welded and integrated with the outer peripheral surface of the shaft member. According to this method, the high alloy component of the outer layer does not mix into the shaft member during welding to deteriorate its toughness, and a tough low alloy steel can be used as the shaft member, which is preferable.

On the other hand, as a high wear-resistant cast iron material for outer layer casting, as disclosed in JP-A-4-176840, a high speed cast iron material having the following chemical composition (wt%) is known. C: 1.0 to 3.0%, Si: 0.1 to 2.0%, Mn:
0.1 to 2.0%, Cr: 3.0 to 10.0%, Mo: 0.1 to 6.
0%, W: 1.5 to 10.0%, V or Nb, one or two kinds in total: 3.0 to 10.0%, balance substantially Fe The high speed cast iron material containing Mo, W and V has high temperature characteristics. It has excellent wear resistance and rough skin resistance because it has excellent hardness and crystallized carbides with high hardness such as VC, M ₂ C, M ₆ C, etc. Used as an outer layer material for composite rollers.

[0004]

However, the conventional high-speed cast iron material has a large friction coefficient, and as a result, there are problems such as an increase in rolling load, an unbalance in stripability, and heat generation. The passability means the easiness of separation of the rolled plate from the roll surface.If this is not the case, the rolled plate will stick to the roll surface, hinder smooth running and meander. , Surface damage such as wrinkles occurs. Further, when an excessive load is applied to the roll during rolling, there is a problem that microcracks generated on the surface of the roll easily propagate inside the outer layer after that, and in extreme cases, the outer layer is broken.

The present invention has been made in view of the above problems,
An object of the present invention is to provide a method for manufacturing a composite rotating member such as a composite roll in which the outer layer has a low coefficient of friction and cracks are less likely to develop.

[0006]

According to the method of manufacturing a composite rotary member of the present invention, a shaft member made of a tough material is continuously and concentrically lowered in a cylindrical mold to form a gap between the mold and the shaft member. In the method for producing a composite rotating member, in which the outer layer material is continuously poured into and solidified in the lower part of the mold to integrally form the outer layer by welding on the outer peripheral surface of the shaft member, the chemical composition of the outer layer material is wt%. C: 1.8-3.6%, Si: 1.0-3.5%, Mn:
0.1 to 2.0%, Ni: 0.5 to 10.0%, Cr: 2.0 to 10
%, Mo: 0.1-10%, W: 0.1-10%,
V, Nb: A high-speed cast iron material having one or two kinds of graphite in total of 1.5 to 10% and the balance being substantially Fe is used. At this time, in addition to the above alloy components, Co: 0.5-
10.0 wt% or Al: 0.01 to 0.50 wt%, Ti: 0.01 to 0.
One or two of 50 wt% and Zr 0.01 to 0.50 wt% or B: 0.01 to 0.50 wt% can be contained. Also,
A steel material having excellent toughness may be used as the shaft member.

[0007]

According to the present invention, since the outer layer is cast on the outer peripheral surface of the shaft member by the continuous build-up welding method, the outer layer material molten metal is stirred by the heating of the high frequency induction heating coil during solidification in the mold, and the outer layer structure is formed. Becomes fine. Further, since the shaft member is pre-processed and an appropriate tough material such as various steel materials can be used, it is easy to improve the strength and toughness of the shaft member. Further, when the outer layer is welded, there is no risk that the high alloy component of the outer layer material will be mixed into the shaft member, and there is no risk that the toughness of the shaft member will deteriorate.

In the high-speed cast iron material of the outer layer material according to the present invention, since a high hardness composite carbide in which Cr, Mo, W, Nb, V, Fe and C are mutually bonded is present in the matrix, By strengthening the base with Co, hardness at room temperature and high temperature is improved, and wear resistance is dramatically improved.
Furthermore, since C, Si, and Ni are specified in a specific range, graphite crystallizes and precipitates in the structure in an area ratio of about 0.1 to 7.0%, and the impact load can be relaxed by the action of this graphite. In addition, cracks can be prevented from progressing, and the coefficient of friction can be reduced and seizure resistance can be improved. In particular, according to the continuous build-up welding method, it is possible to increase the solidification rate, the crystallized graphite becomes finer, and it is possible to suppress wear starting from graphite, wear resistance, and rough surface resistance. Can be improved. Therefore, the composite roll produced by the present invention can exert the excellent characteristics of the outer layer material during rolling, reduction of rolling load and frictional heat, improvement of stripability, and improvement of cracks are suppressed. obtain. Since this rolling roll has good seizure resistance due to the action of graphite, it is also suitable as a cold rolling roll. Further, according to the present invention, it is possible to suitably provide a rotating member such as a composite roller used in an auxiliary equipment for rolling.

[0009]

EXAMPLES First, the reasons for limiting the chemical composition of the high speed cast iron material having graphite according to the present invention will be explained. Less than,
All units of components are wt%. C: 1.8 to 3.6% C mainly combines with Fe and Cr to form a M ₇ C ₃ type high hardness composite carbide, and also contains Cr, Mo, V, N.
It also combines with b and W to form high hardness composite carbides such as MC type, M ₆ C type and M ₂ C type. Further, due to the action of Si, which is a graphitization-promoting element described later, and by heat treatment, fine graphite is formed and crystallizes and precipitates in the structure. If it is less than 1.8%, the amount of carbides will decrease and graphite will almost disappear.
If the content exceeds 3.6%, the amount of carbide and the amount of graphite become excessive and the material becomes brittle.

Si: 1.0 to 3.5% Si is an element necessary for ensuring the flowability of molten metal and crystallizing and precipitating graphite. If it is less than 1.0%, the action is insufficient, while if it exceeds 3.5%, graphite is not formed. The area ratio exceeds 7%, resulting in excessive wear starting from graphite and deterioration in wear resistance. In order to promote crystallization of graphite, it is preferable that the amount of Si before casting is made lower than the above-mentioned range of components, inoculation is performed at the time of casting, and the components of the final product are adjusted to be within the above range.

Mn: 0.1-2.0% Mn is an element that increases the hardening ability and also combines with S to form MnS to prevent embrittlement due to S. At the same time, 0.1% is inevitably contained from the raw materials used. To be done. But 2.0
%, It is not preferable because the toughness is deteriorated. Ni: 0.5-10.0% Ni is added for the purpose of improving the matrix structure and crystallizing and precipitating graphite. If it is less than 0.5%, the amount of graphite is too small.
If it exceeds 0.0%, too much graphite will be produced, as in the case of Si.
Further, the retained austenite increases, it becomes difficult to form a tough structure even by the subsequent heat treatment, and the wear resistance deteriorates.

Cr: 2.0-10% Cr combines with C together with Fe, Mo, V, Nb and W,
It forms a high hardness composite carbide and contributes to the improvement of wear resistance at high temperatures. In addition, some of them form a solid solution in the matrix to improve hardenability and wear resistance. If it is less than 2.0%, these effects are small, while if it exceeds 10%, toughness is deteriorated, which is not preferable.

Mo: 0.1-10% Mo easily bonds with C along with Fe, Cr, V, Nb and W.
And mainly M₇C ₃Mold, M₆C type, M₂C type composite coal
To increase wear resistance by increasing the hardness at room temperature and high temperature.
Contribute to improvement. Mo is effective when added in a small amount compared to W
Exert fruit. In this case, if less than 0.1%, the effect is excessive.
On the other hand, if it exceeds 10%, the toughness decreases, which is preferable.
No

W: 0.1 to 10% Similarly, W also easily combines with Fe, Cr, Mo, V, and Nb to form C to form a composite carbide, which contributes to improvement of wear resistance by increasing hardness at normal temperature and high temperature. To do. If it is less than 1.5%, the desired wear resistance cannot be obtained, while if it exceeds 10.0%, the toughness is lowered and the heat crack resistance is deteriorated.

V, Nb: 1.5 or 10 in total of one or two
% V, like Nb, easily combines with C along with Fe, Cr, Mo, and W to mainly form MC type composite carbides, which increases the room temperature and high temperature hardness and contributes to the improvement of wear resistance.
Further, since this MC type composite carbide is formed in a branch shape in the thickness direction, it suppresses plastic deformation of the matrix and contributes to improvement of mechanical properties and crack resistance. Such effects are unlikely to be exhibited unless 1.5% or more is added alone or in combination of two kinds. However, if the addition amount exceeds 10%, the toughness is lowered.

The high-speed cast iron material according to the present invention is formed of Fe and the unavoidably mixed impurities in addition to the above alloy components. In addition, P and S are inevitably mixed from the raw material, but it is desirable to reduce P and S because it makes the material brittle.
It is better to keep it below 2% and S: 0.1% or less. In the cast iron material according to the present invention, in addition to the alloy components, if necessary, Co: 0.5 to 10.0%, or / and one or more of Al, Ti, and Zr in the following composition range, or / And B: 0.01 to 0.50% can be contained.

Co: 0.5-10.0% Co has a great effect on improving the base. Co is C
Has a special effect of suppressing the diffusion of carbon and has the effect of increasing the toughness by forming a solid solution in the matrix irrespective of the formation of carbides and improving the high temperature hardness and wear resistance. Further, Co increases the solid solution amount of the carbide forming element in the austenite, so that the hardness of the matrix and the tempering resistance increase. In order to expect these effects, 0.5% or more must be contained, but 10.0
Even if added in excess of%, the effect is saturated, and since it is an expensive element, it is 0.5 to 10.0%.

Al, Ti, Zr: 0.01 to 0.50% Al, Ti, Zr form oxides in the molten metal, reduce the oxygen content in the molten metal, improve the soundness of the product, and form Since the oxide thus formed acts as a crystal nucleus, it is effective in refining the solidified structure. If it is less than 0.01%, this effect is not sufficient, while if it exceeds 0.50%, it remains as inclusions, which is not preferable. In addition, Al, Ti,
In the present invention, Zr is mainly added to improve wear resistance by refining the cast structure, and is not simply added for degassing.

B: 0.01 to 0.50% B exhibits a deoxidizing effect by combining with oxygen in the molten metal. In addition, the effect of refining the solidified structure with the generated oxide as the core,
Also, it has the effect of increasing the hardenability due to B dissolved in the matrix. In the case of a casting having a large mass such as a rolling roll, it may be difficult to increase the cooling temperature, but an increase in hardenability makes it easier to obtain a hardened structure. If it is less than 0.01%, such an effect is not sufficient, while if it exceeds 0.50%, the material becomes brittle, which is not preferable.

The present invention is a composite cylinder such as a two-layer composite roll or a two-layer composite roller obtained by welding and integrating an outer layer made of the above-mentioned high speed cast iron material on the outer peripheral surface of the shaft member by the continuous build-up welding method described above. Although the member is manufactured, either solid or cylindrical shape can be used as the shaft member, and its material is high-grade cast iron, ductile cast iron, graphite steel, cast steel (C: 1.0% or more) ) And other tough steels for casting, and tough steels such as forged steels, carbon steels for machine structures (SC materials), low alloy steels for machine structures (SCM materials, SNCM materials, etc.) can be used as appropriate. it can. In addition, on the outer peripheral surface of the shaft member
It is preferable to form the plating to a thickness of several μm to 20 μm because surface oxidation of the shaft member can be prevented and the weldability with the outer layer can be improved.

When the shaft member is formed of flake graphite cast iron, spheroidal graphite cast iron, or graphite steel, that is, a steel material in which graphite is crystallized, combined with the presence of graphite in the outer layer, it is excellent in thermal conductivity and thus heat dissipation, and is excellent in rolling. It is possible to prevent thermal deformation of the roll. The Young's modulus of these materials is 19000 kgf /
Since it is about mm ² or less and can be made considerably lower than that of the outer layer, it is possible to absorb the load by flattening the roll at the time of overload and prevent excessive stress from being generated in the outer layer. Further, since it has good toughness, it can withstand shocking rolling torque, is easy to control the bender of the neck part, and has a large shock absorbing ability, which is preferable.

Preferred composition examples (wt%) of high-grade cast iron, ductile cast iron and graphite steel are shown below. High grade cast iron C: 2.5 to 4.0%, Si: 0.8 to 2.5%, Mn:
0.2 to 1.5%, P: 0.2% or less, S: 0.2% or less, Ni: 3.0% or less, Cr: 2.0% or less,
Mo: 2.0% or less, balance: substantially Fe. Ductile cast iron C: 2.5-4.0%, Si: 1.3-3.5%, Mn:
0.2 to 1.5%, P: 0.2% or less, S: 0.2% or less, Ni: 3.0% or less, Cr: 2.0% or less,
Mo: 2.0% or less, Mg: 0.02 to 0.1%, balance: substantially Fe / graphite steel C: 1.0 to 2.3%, Si: 0.5 to 3.0%, Mn:
0.2 to 1.5%, P: 0.2% or less, S: 0.2% or less, Ni: 3.0% or less, Cr: 2.0% or less,
Mo: 2.0% or less, W, V, Nb: 4.0% or less in total, the balance: substantially Fe The high-speed cast iron material having graphite according to the present invention is a hardening temperature after overlay casting as an outer layer of a composite cylindrical member. The temperature range from (austenizing temperature) to 400 to 650 ℃ is 100 ℃
By quenching at a cooling rate of / Hr or higher, a good quenched structure can be obtained. The tempering may be performed once to several times at a temperature of 500 to 600 ° C. The outer layer material according to the present invention has a high temperature hardness because Mo, W, V, Nb, etc. solid-soluted in the matrix during the austenitizing heat treatment are precipitated as fine carbides by the tempering heat treatment and cause a secondary hardening phenomenon of the tempering. Excel. Further, graphite is precipitated in the structure by the tempering heat treatment.

As a method for heating the outer layer, a method in which the entire cylindrical member is placed in a heating furnace for heating, an induction heating coil and a number of gas burners are arranged around the outer peripheral surface of the outer layer, and only the outer layer is rapidly heated by these. There is a way. In the former case, it takes time to raise the temperature, a thick oxide film is formed on the outer layer surface, and the yield of the outer layer decreases. Furthermore, when the shaft member is made of cast iron material, it is necessary to heat the shaft member at 1100 ° C to avoid melting damage and heat it.
It is necessary to stop the heating at a temperature (preferably 1000 ° C.) or less, which makes it difficult to sufficiently dissolve the carbide in the matrix, and it is difficult to obtain sufficient hardness by the subsequent heat treatment. On the other hand, according to the heating method of only the outer layer, the outer layer (portion up to the vicinity of the welded portion) can be stopped at 1100 ° C or higher, and the shaft member can be stopped at less than 1100 ° C.
It is possible to prevent partial melting of the shaft member and strength reduction due to coarsening of crystal grains. Further, since the temperature becomes lower toward the center of the shaft member, the heat of the outer layer can be released to the inside after heating to the austenitizing temperature, and the cooling rate of the deep portion of the outer layer can be increased during quenching.

Next, specific examples of the present invention will be given. A shaft member having an outer diameter of 300 mm was manufactured from a bar material of low alloy steel (SCM440) and ductile cast iron (DCI). The shaft member is passed through a overlay welding mold and heated to 650 to 6 by a heating coil.
After preheating to 80 ° C, increase the output of the coil so that the surface temperature becomes about 1050 ° C, and close the cylindrical casting space inside the mold with the disk attached to the lower end of the shaft member while keeping the shaft member inside the mold. While being lowered, the molten metal for the outer layer material (casting temperature: 1400 ° C.) shown in Table 1 below was continuously injected from the upper opening of the mold so that the molten metal surface became constant. At this time, the surface of the molten metal filled around the shaft member in the upper part of the mold was covered with flux. Sample Nos. 1 to 5 are examples, No. 6 is a conventional example, and the material of the shaft member is Nos. 1 to 3.
Is SCM440 and Nos. 4 to 6 are DCI.

[0025]

[Table 1]

The shaft member was lowered at a speed of 30 mm / min, and the outer layer was welded and integrated with the shaft member while solidifying the molten metal in a water-cooled mold under the mold. After pouring a predetermined amount of molten metal, the pouring was stopped and the shaft member was pulled out from below the mold to obtain a composite roll having an outer layer formed on the outer peripheral surface of the shaft member. When the composite roll was subjected to an ultrasonic flaw detection test, it was confirmed that the shaft member and the outer layer were completely welded.

Next, a test piece was sampled from the outer layer of each roll, and the microstructure was microscopically observed to measure the area ratio of crystallized graphite. The results are shown in Table 2. From the table, graphite was generated in an area ratio of 3.9 to 5.1% in the examples, but no graphite crystallization was found in the conventional high speed wear-resistant material.

[0028]

[Table 2]

After holding each test piece at 1100 ° C. for 1 hour, it was quenched by forced air cooling, and thereafter, a tempering heat treatment at 540 ° C. for 10 hours was repeated 3 times. The surface hardness of each sample was measured. Further, a round bar test piece was sampled from each test piece, and the friction coefficient was measured by the Falex test. The Falex test is a test in which a test piece is rotated and nipped and pressed by a pair of V blocks (material stainless steel SUS430), and the friction coefficient and seizure property are examined by the magnitude and fluctuation of the rotation torque. The material of the block used this time was S45C, the pressing force was 30 kgf, the rotation speed was 300 rpm, and the test time was 1 minute.

The results are also shown in Table 2. From the same table, the outer layer materials of the examples had no seizure, but the conventional example showed seizure, and the coefficient of friction was reduced by 17 to 34% as compared with the conventional example.

[0031]

According to the manufacturing method of the present invention, any tough material can be used as the shaft member, and there is no fear that the high alloy component of the outer layer material will be mixed into the shaft member during welding with the outer layer, The toughness of the member does not deteriorate. Further, the high speed cast iron material having graphite forming the outer layer material is made of Cr, M
O, W, Nb, V, Fe and C are bonded to each other to form a high hardness composite carbide in the matrix, and the strengthening of the matrix by Co improves the hardness at normal temperature and high temperature, resulting in wear resistance. Improve dramatically. Furthermore, especially C, S
Since i and Ni are defined in specific ranges, graphite crystallizes and precipitates in the structure, and the action of this graphite can alleviate the impact load and prevent the development of cracks.
Further, the friction coefficient is reduced and the seizure resistance is improved.

─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. ⁶ Identification number Internal reference number FI Technical indication C22C 37/00 B 37/08 A (72) Inventor Cho Morikawa 64 Nishimukojima-cho, Amagasaki-shi, Hyogo Stock Company Kubota Amagasaki Factory

Claims (5)

[Claims] 1. A shaft member made of a tough material is continuously and concentrically lowered into a cylindrical mold, and the outer layer molten metal is continuously injected into a gap between the mold and the shaft member and solidified at the bottom of the mold. In the manufacturing method of the composite rotating member, wherein the outer layer is integrally formed by welding on the outer peripheral surface of the shaft member, the chemical composition of the outer layer material is wt%, and C: 1.8 to 3.6%,
Si: 1.0-3.5%, Mn: 0.1-2.0%, Ni:
0.5-10.0%, Cr: 2.0-10%, Mo: 0.1-
10%, W: 0.1 to 10%, V, Nb: 1.5 to 10% in total of one or two kinds, and the balance is a manufacturing method of a HSS-based composite rotating member having graphite composed of Fe. 2. In addition to the alloy components of claim 1, Co: 0.5
To manufacture a HSS-based composite rotating member having graphite containing about 10.0 wt%. 3. In addition to the alloy components of claim 1, Al: 0.01
~ 0.50wt%, Ti: 0.01 ~ 0.50wt%, Zr: 0.01 ~ 0.50
A method for manufacturing a HSS-based composite rotating member having graphite containing one or two of wt%. 4. In addition to the alloy components of claim 1, B: 0.01-
A method for manufacturing a HSS-based composite rotating member having graphite containing 0.50 wt%. 5. The method for producing a HSS-based composite rotating member having graphite according to claim 1, 2, 3 or 4, wherein the shaft member is formed of steel.