KR20120078757A - Maraging steel and maraging steel for metallic belt - Google Patents

Abstract

The present invention provides a composition capable of reducing TiN, which is a starting point of fatigue failure in a high cycle region, and facilitates nitriding treatment, increases surface hardness, and increases the compressive residual stress of the surface nitride layer to increase bending fatigue. Provided is a maraging steel for metal belts, in which the old austenite grains are refined in order to improve the strength and to secure high strength and ductility. By mass%, C: 0.01% or less, Si: 0.1% or less, Mn: 0.1% or less, P: 0.01% or less, S: 0.005% or less, Ni: 17.0-22.0%, Cr: 0.1-4.0%, Mo: 3.0 7.0%, Co: more than 7.0% and 20.0% or less, Ti: 0.1% or less, Al: 2.5% or less, N: 0.03% or less, O: 0.005% or less, B: 0.01% or less (0 is not included), Co / 3 + Mo + 4Al: 8.0-15.0%, The remainder is a maraging steel composed of Fe and unavoidable impurities.

Description

MARINGING STEEL AND MARAGING STEEL FOR METALLIC BELT}

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to maraging steel having excellent fatigue strength and metalizing belt for metal belts used in continuously variable transmissions for automobiles and the like.

Since maraging steels generally have very high tensile strengths of around 2000 MPa, the components requiring high strength, for example, parts for rockets, centrifuge parts, aircraft parts, parts for continuously variable transmissions in automobile engines. It is used for various uses, such as a metal mold | die. As the typical composition, 18% Ni-8% Co-5% Mo-0.4% Ti-0.1% Al-bal.Fe can be mentioned.

The maraging steel contains Co, Mo, and Ti as appropriate strengthening elements, and by aging treatment, intermetals such as Ni ₃ Mo, Ni ₃ Ti, Fe ₂ Mo, and the like are subjected to aging treatments. It is a steel that can obtain high strength by depositing intermetallic compounds. In particular, in steel strips used in parts for continuously variable transmissions of automobile engines, since fatigue strength is a particularly important characteristic in high cycle areas, TiN and the like present in maring steel having high strength are required. It is necessary to make the nonmetallic inclusions as small as possible. In addition, nitriding is performed on the surface to form a nitride layer to improve fatigue strength.

In the metal belt for continuously variable transmissions of automobile engines, improved alloys for the purpose of solving fatigue strength reductions having non-metallic inclusions as a starting point (for example, Patent Documents 1, 2, and 3) have been proposed. Reference).

Patent Document 1: Japanese Patent Application Publication No. 2004-514056

Patent Document 2: Japanese Patent Application Publication No. 2001-240943

Patent Document 3: Japanese Patent Application Publication No. 2002-167652

The alloy disclosed in Japanese Patent Application Laid-Open No. 2004-514056 described above reduces the Ti forming the nonmetallic inclusion to 0.1% or less. Therefore, although it is advantageous in terms of miniaturization of TiN, which is the starting point of fatigue failure, there is a problem that nitriding treatment is difficult to perform in order to perform an alloy which simply suppresses the addition of an element forming a nonmetallic inclusion.

In addition, the alloy disclosed in Japanese Patent Application Laid-open No. 2001-240943 also reduces Ti, which is advantageous in terms of miniaturization of TiN, which is a starting point of fatigue failure. However, since Co, which is one of the reinforcing elements, is kept low, it is difficult to secure high tensile strength. Moreover, although Si and Mn are added in order to ensure tensile strength, there exists a possibility that toughness may fall because of this.

In addition, the alloy disclosed in Japanese Patent Application Laid-open No. 2002-167652 also reduces Ti, which is advantageous in terms of miniaturization of TiN, which is a starting point of fatigue failure. However, since C is actively added to increase the strength, carbides such as Cr and Mo are precipitated, which is the starting point of fatigue breakdown, and the fatigue strength is lowered, or the weldability required for the continuously variable transmission parts is lowered by C added positively. There is a possibility.

An object of the present invention is to provide a composition capable of reducing TiN, which is the starting point of fatigue failure in a high cycle region, to facilitate nitriding treatment, to increase surface hardness, and to increase the compressive residual stress of the surface nitride layer. In order to improve fatigue bending-strength and further secure high strength and ductility, the maraging steel and the maraging steel which are made of fine austenite grains are used. It is to provide a maraging steel for a metal belt formed by.

MEANS TO SOLVE THE PROBLEM In order to reduce TiN which is an interference | inclusion harmful to fatigue strength improvement, this inventor suppresses Ti and N together low and increases the Co and Mo by the fall of the strength by Ti reduction, and adds to Co and Mo as needed and Al In addition, it was found that compensation can also be made by limiting the value of Co / 3 + Mo + 4Al to an appropriate range. In addition, in order to improve tensile strength, ductility, and fatigue strength, it has been found that grain refinement is effective, but this can be solved by adding a trace amount of B.

In addition, the present inventors have found that the absolute value of the surface compressive residual stress due to nitriding can be increased by adding an appropriate amount of Cr or by adding an appropriate amount of Cr and Al in order to solve the difficulty of nitriding treatment caused by Ti reduction. In addition, by suppressing C to an impurity level, weldability is ensured and the present invention is reached.

That is, in the present invention, C: 0.01% or less, Si: 0.1% or less, Mn: 0.1% or less, P: 0.01% or less, S: 0.005% or less, Ni: 17.0-22.0%, Cr: 0.1-4.0 %, Mo: 3.0-7.0%, Co: 7.0% or more 20.0% or less, Ti: 0.1% or less, Al: 2.5% or less, N: 0.03% or less, O: 0.005% or less, B: 0.01% or less Not included), Co / 3 + Mo + 4Al: 8.0-15.0%, remainder is maraging steel which consists of Fe and an unavoidable impurity.

In the present invention, in order to achieve the above object, there are two preferred compositions. The first preferred composition is one in which Al is positively added within the range of the basic composition described above.

That is, the 1st preferable composition of this invention is the maraging steel of the composition which makes Cr and Al in mass% Cr: 0.1-3.0%, Al: 0.15% or more and 2.5% or less in the composition mentioned above.

Preferred ranges of the composition in which Al is positively added are C: 0.008% or less, Ni: greater than 18.0% and 22.0% or less, Mo: greater than 5.0% and 7.0% or less, Ti: 0.05% or less, Co / 3 + Mo + 4Al: It is a maraging steel with 10.0 to 15.0%.

Moreover, it is preferable that it is maraging steel which is Co: more than 12.0% and 20.0% or less by mass%.

In addition, in this invention, in addition to the composition which positively adds Al mentioned above, as a 2nd preferable composition, it adjusts to the composition range which contains a little Co, restricting Al within the range of the above-mentioned basic composition.

That is, the 2nd preferable composition of this invention is Co: Ti, Al in mass% of the above-mentioned composition, Co: 10.0% or more, 20.0% or less, Ti: 0.05% or less, Al: less than 0.1%, Al + Ti: Maraging steel to be less than 0.1%.

In the present invention, in addition to the above-described basic composition, first preferred composition and second preferred composition, one or more kinds may be further contained in mass% of Ca: 0.01% or less and Mg: 0.005% or less.

The present invention is also a maraging steel having a grain size of 10 or more fine grains in ASTM No.

Moreover, this invention is the maraging steel for metal belts which uses the maraging steel mentioned above.

The maraging steel of the present invention can reduce TiN, which is the starting point of fatigue failure, and obtain high strength, high hardness of the surface after nitriding treatment, and large compressive residual stress, so that power transmission used in a continuously variable transmission for automobiles When used in a member that requires high fatigue strength, such as a metal belt, it is expected to have a remarkable effect in industrial aspects, such as having a long fatigue life.

1 is an electron micrograph of the surface of the maraging steel to which Al of the present invention is positively added.
2 is an electron micrograph of the surface of maraging steel with limited addition of Al of the present invention.

This invention is made | formed based on the novel knowledge mentioned above, and the effect | action of each element in this invention is demonstrated below.

In the maraging steel of this invention, the reason which prescribed | regulated each chemical composition in the following ranges is as follows. And unless otherwise indicated, it describes by mass%.

C forms carbide with Mo, reduces the intermetallic compound to be precipitated, and lowers the strength. Therefore, C needs to be kept low. In addition, when C is positively added, there is a high risk that the weldability required for, for example, the continuously variable transmission component is lowered. For this reason, C was made 0.01% or less. The preferred range is 0.008% or less.

Si is an element which can supplement the intensity | strength decrease by Ti fall by refine | miniaturizing the intermetallic compound which precipitates at the time of aging treatment, or forming an intermetallic compound with Ni. However, since the toughness may be lowered, in order to secure toughness and ductility, it is necessary to suppress it low in the present invention. When it exceeds 0.1%, since toughness and ductility fall, Si was made into 0.1% or less. A preferable range for more reliably securing toughness and ductility is 0.05% or less.

Mn is an element which forms an intermetallic compound with Ni at the time of aging treatment and contributes to aging hardening, and thus Mn is an element capable of supplementing the strength-decreasing amount due to Ti reduction. However, since the toughness may be lowered, in order to secure toughness and ductility, it is necessary to suppress it low in the present invention. If it exceeds 0.1%, toughness and ductility will fall, Mn was made into 0.1% or less. A preferable range for further securing the toughness and the ductility is 0.05% or less.

P and S are harmful elements which segregate at the old austenite grain boundary or form inclusions to weaken the maraging steel and lower the fatigue strength. Therefore, P is 0.01% or less and S is 0.005% or less. It is preferably in the range of 0.005% or less for P and 0.004% or less for S.

Cr is an element that has a high affinity with N for nitriding, has a shallow nitriding depth, increases nitriding hardness, or increases compressive residual stress on the nitriding surface, and therefore, is essentially added. However, if it is less than 0.1%, there is no effect. On the other hand, even if it adds exceeding 4.0%, more effects are not always seen, and since the intensity | strength after age falls significantly, Cr was made into 0.1 to 4.0%. And when adding Al positively, the upper limit of Cr is sufficient as 3.0%. Ni stably forms a low C martensite structure, which is a matrix structure of maraging steel, and therefore at least 17.0% is required. However, if it exceeds 22.0%, the austenite structure is stabilized and martensite transformation is not easily caused, so Ni is 17.0-22.0%. The preferable range of Ni is more than 18.0% and 22.0% or less.

Mo is an important element which forms fine intermetallic compounds such as Ni ₃ Mo, Fe ₂ Mo during the aging treatment and contributes to precipitation strengthening. In addition, Mo is an effective element for increasing the hardness and compressive residual stress of the surface by nitriding. Mo is less than 3.0%, and the tensile strength is insufficient, while more than 7.0%, it is easy to form coarse intermetallic compounds containing Fe and Mo as main elements, so Mo is 3.0 to 7.0%. It was. The preferable range of Mo is more than 5.0% and 7.0% or less.

Co does not significantly affect the stability of the martensite structure of the matrix and increases the solubility of aging precipitate-forming elements such as Mo and Al at the solubilization treatment temperature, and Mo at the aging precipitation temperature range. , Al is an important element that promotes precipitation of fine intermetallic compounds containing Mo and Al by lowering the solubility of Al and contributes to aging precipitation strengthening. Therefore, Co needs to be added a lot in consideration of strength and toughness. If Co is less than 7.0%, it is difficult to obtain sufficient strength with maraging steels with reduced Si, Mn, and Ti. On the other hand, when it is added more than 20.0%, austenite is stabilized and it is difficult to obtain martensite structure. It was set as 20.0% or less. Preferred range of Co is more than 12.0% and 20.0% or less.

In addition, when limiting Al, it is desirable to limit Al slightly, which contributes to strengthening. Therefore, the range of Co is made more than Co: 10.0% and 20.0% or less.

Ti is one of the important reinforcing elements in maraging steels, but at the same time, TiN or Ti (C, N), which is an inclusion, forms harmful substances, and in particular, reduces the fatigue strength in ultra high cycle regions. Therefore, when Ti stresses fatigue strength, it is necessary to restrain Ti low.

In addition, since Ti is easy to form a thin and stable oxide film on the surface, and this oxide film is formed, the nitriding reaction is inhibited, and it becomes difficult to sufficiently obtain the compressive residual stress on the nitride surface. In order to facilitate nitriding and to increase the compressive residual stress on the surface after nitriding, Ti is a harmful impurity element and needs to be kept low.

If Ti is more than 0.1%, an effect sufficient for reducing TiN or Ti (C, N) cannot be obtained, and since a stable oxide film is easily formed on the surface, Ti is made 0.1% or less. It is preferable to set it as 0.05% or less, and it is more preferable to set it as 0.01% or less.

Al is two types in the case of this invention, and the case where it adds actively and a case where it limits.

When Al is positively added, the strength of the maraging steel can be improved. Therefore, when emphasis is placed on strength, it is better to add Al actively. The Al content in the case of adding positively is demonstrated.

Al is usually added in small amounts for deoxidation, but is originally an element that contributes to strengthening by forming an intermetallic compound together with Ni during aging treatment. In the maraging steel for metal belts of this invention which reduced Si, Mn, and Ti, it is preferable to supplement strength by addition of Al. In addition, since nitriding is easy in maring steels with reduced Ti, the addition of Al is necessary to obtain a good nitride layer. Al does not obtain sufficient reinforcing action by aging treatment at 0.15% or less, whereas when it is more than 2.5%, AlN and Al ₂ O ₃ inclusions are formed to reduce fatigue strength, or thin and stable oxide film is formed on the surface to nitride. Since the reaction was inhibited, Al was made more than 0.15% and 2.5% or less. And when Al is positively added, the maraging steel surface roughness may become slightly rough. Therefore, the preferable upper limit in the case of adding Al positively is made into 1.5%.

By restricting the content of Al, nonmetallic inclusions in the maraging steel can be reduced. In addition, since the roughness of the surface of the maraging steel made of Al becomes easy to be maintained flat, it is preferable to limit Al when the origin of fatigue failure is reduced and the importance of fatigue strength is important. Preferable content at the time of restricting Al is demonstrated.

Al may combine with oxygen and nitrogen to form a non-metallic inclusion and reduce the fatigue strength. Therefore, Al may be suppressed to a low level when stress is important. When Al is added 0.1% or more, AlN and Al ₂ O ₃ inclusions are easily formed, and the fatigue strength may be lowered. Therefore, Al may be limited to less than 0.1%. The preferred range of Al is 0.05% or less.

In addition, since Al and Ti are both elements which form a nonmetallic inclusion, since low total amount of Al + Ti is effective for improving fatigue strength, Al + Ti is made into 0.1% or less. The preferable range of Al + Ti is 0.07% or less.

Co, Mo, and Ti are all major reinforcement elements in maraging steel, and Al is also an element contributing to aging reinforcement of maraging steel. When Ti is suppressed low, it is necessary to replenish the decrease in strength due to Ti by increasing the addition amount of Co and Mo, or by increasing the addition amount of Al in addition to Co and Mo when Al is actively added. However, the contribution to the strengthening of each element is not the same, and the strengthening by Co and Al are 1/3 and 4 times the strengthening by Mo, respectively.

Therefore, the strengthening by Co, Mo, and Al can be summarized as Co / 3 + Mo + 4Al. If the value of Co / 3 + Mo + 4Al in mass% is less than 8.0%, the strength is not sufficient, while if it exceeds 15.0%, the strength is too high, and there is a fear of toughness. It was set as 8.0-15.0%. Preferred Co / 3 + Mo + 4Al is in the range of 10.0-15.0%.

N is an impurity element which binds to Ti to form inclusions of TiN or Ti (C, N), and particularly lowers the fatigue strength in the ultrahigh cycle region. In maraging steel containing Ti, it is necessary to suppress N significantly in order to prevent formation of coarse TiN or Ti (C, N). However, in the maraging steel that does not substantially contain Ti, even if the amount of N mixed by ordinary vacuum melting is less adversely affected, it is set at 0.03% or less. The range of 0.01% or less is preferable, and the range of 0.005% or less is more preferable.

O is an impurity element that forms oxide inclusions and lowers toughness and fatigue strength, and is therefore limited to 0.005% or less. 0.003% or less is preferred.

B is an element which has an effect which refine | miniaturizes the old austenite crystal grain at the time of performing a solid solution treatment after cold working, and contributes to reinforcement, and suppresses roughness of a surface, and is added essentially. If B is more than 0.01%, toughness is lowered, so B is made 0.01% or less (0% is not included). 0.005% or less (0% is not included) is preferable. The minimum with preferable B which can refine | refine a former austenite crystal grain more reliably is 0.0002%, and a more preferable minimum is 0.0003%.

In the present invention, at least one of Ca: 0.01% or less and Mg: 0.005% or less can be contained.

The maraging steel of the present invention can produce an ingot by vacuum induction melting or vacuum induction melting and further dissolution in a vacuum atmosphere such as vacuum arc remelting or electro slag redissolution. have. However, even when dissolving in these vacuum atmospheres, it is technically difficult to completely remove the nonmetallic inclusions.

In the present invention, since Al may be actively added for the purpose of improving the strength, for example, there is a risk that coarse and hard Al ₂ O ₃ inclusions exceeding 25 μm are formed, but Al ₂ O ₃ clusters. There is a risk of becoming angry. Al ₂ O ₃ inclusions are hard and high melting points, and do not substantially deform even during hot plastic working. Therefore, for example, there is a possibility that a flaw may be generated in the roll during cold rolling, which may cause surface defects of the maraging steel for metal belts. Therefore, the Al ₂ O ₃ inclusion is made into a composite inclusion with another oxide to reduce the hardness. Or lower the melting point. At the same time, it is preferable to add an element capable of preventing clustering to prevent inclusion defects.

Examples of effective elements for making the Al ₂ O ₃ inclusions a composite inclusion include Si, Mn, Ca, and Mg. In the present invention, Si and Mn are elements that reduce toughness and ductility, and the amount of addition is controlled. Therefore, it is preferable to make an Al ₂ O ₃ inclusion into a composite inclusion by adding at least one of Ca and Mg other than Si and Mn. In addition, Ca and Mg also have an effect of preventing clustering of Al ₂ O ₃ inclusions. Therefore, in the present invention, Ca: 0.01% or less, or Mg: 0.005% or less.

In order to reliably obtain the effects of Ca and Mg, Ca is preferably 0.001% and Mg is 0.0001%.

As mentioned above, it is set as Fe and an unavoidable impurity except the element demonstrated.

And the following elements may be added for the purpose of deoxidation, deoiling, etc. as long as it is in the following range.

Zr≤0.01%

In the maraging steel of the present invention, after cold working at least 10%, by solidifying the solution to a suitable temperature according to the composition, for example, about 780 ~ 1000 ℃ (formerly, in the case of maraging steel, Old austenite grains) may be refined to ASTM No. 10 or higher.

In the maraging steel of the present invention, by refining the grains, the hardness, tensile strength, fatigue strength, impact toughness, and the like can be stably increased, but in the steel strip, surface roughness can be made light. You can expect the effect of.

As mentioned above, the maraging steel of this invention contains Al in 2.5% or less of range.

In the maraging steel of this invention, as a new knowledge, the characteristic phenomenon in which the shape of the surface of a maraging steel becomes rough according to Al content was acquired. This is presumed to be the reason that Al having a high diffusion coefficient is caused to concentrate on the surface by high temperature heat treatment such as solid solution heat treatment and the atmosphere, thereby causing surface oxidation.

If the surface shape becomes rough, for example, when the maraging steel of this invention is used for the power transmission metal belt used for the continuously variable transmission for automobiles, the risk of fatigue destruction on the low cycle side becomes high. Therefore, it is desirable to keep the surface shape by Al as flat as possible.

Particularly, in the maraging steel to which Al is positively added, the surface of the maraging steel can be flattened by mechanical polishing or chemical surface etching. However, in the state of the maraging steel, Therefore, it is important to suppress the surface thickening of Al as much as possible.

In the raw material before cold working, since the oxide layer formed on the surface of the raw material is removed, it is considered that the Al thickening layer on the surface is also removed. It is preferable to adjust to the atmosphere which is hard to become nitride. For example, vacuum atmosphere, hydrogen atmosphere, Ar atmosphere, etc. may be sufficient. Among these, it is preferable from a viewpoint of productivity that it is set as hydrogen atmosphere and Ar atmosphere which can process a cold rolled material continuously. Since hydrogen is especially inexpensive, it is preferable to use hydrogen.

Since the maraging steel of the present invention does not substantially contain Ti, which forms a stable oxide film on the surface which may inhibit nitriding, it is possible to obtain conventional gas nitriding, gas soft nitriding, immersion nitriding, ion nitriding, salt bath nitriding, and the like. Various nitriding treatments can be facilitated. In addition, in the marring steel for metal belts which do not contain Ti, Cr and Al having an effect of increasing the nitride hardness and the absolute value of the compressive residual stress of the nitride layer also have an absolute value of the compressive residual stress of the nitride layer that tends to be lowered. As a result, the absolute value of the compressive residual stress of the nitride layer can be increased.

In addition, the maraging steel adjusted within the chemical composition range specified in the present invention described above is formed into a band shape of, for example, 0.5 mm or less to form a steel strip of maraging steel for metal belts, and the steel of maraging steel for metal belts. If the strip is subjected to nitriding under appropriate conditions, it is possible to form a thin nitride layer having a thickness of about 20 to 40 µm on the surface without substantially forming nitride, and to give a large compressive residual stress to the surface, thereby improving fatigue characteristics. You can expect.

The higher the compressive residual stress on the surface, the better the fatigue characteristic is, and the control is made possible by appropriately adjusting the thickness of the nitride layer.

The maraging steel for metal belts of the present invention has high tensile strength, high fatigue strength, and is easily nitrided, and is therefore well suited for metal belts for continuously variable transmissions of automobile engines.

[Example]

The present invention will be described in more detail with reference to the following examples.

The maraging steel and comparative steel of this invention were melt | dissolved in the vacuum induction melting furnace, the 10-kg ingot was produced, and after performing homogenization annealing, it hot-forged. Further, a steel strip having a thickness of about 0.3 mm was produced by hot rolling and cold rolling, and made of maraging steel for metal belts. Subsequently, the solid solution treatment was performed at 820 ° C to 900 ° C, and the aging treatment was further performed at 490 ° C, followed by gas soft nitriding at 450 to 470 ° C under a condition that the nitriding depth was 20 to 40 µm.

And the solubilization process was performed in hydrogen atmosphere. Electron micrographs of 0.3 mm thick steel strip surfaces of Nos. 6 and 15 of the present invention are shown in FIGS. 1 and 2. 1 is a maraging steel to which Al is positively added, and the surface is slightly roughened. However, since the solid solution treatment was performed in a hydrogen atmosphere, the surface defect as the starting point of fracture could not be confirmed.

Fig. 2 shows maring steel with limited Al, and it can be seen that the surface shape is flat.

Table 1 shows the chemical compositions of maraging steel Nos. 1 to 8 (Al positively added), steels No. 11 to 16 (Al limitation), conventional steels and comparative steels No. 21 to 22 of the present invention. Here, comparative steel No. 21 is a conventional steel containing Ti, and comparative steel No. 22 is a maraging steel which does not contain Ti and has no addition of Cr and Al. Either maraging strength C was adjusted to the range of 0.01% or less, and the fall of weldability was prevented. In addition, No. 5 and No. 6 which added Al of the steel of this invention positively added Mg. As for Mg content, No. 5 was 10 ppm and No. 6 was 6 ppm. In addition, Mg was added to the steel Nos. 15 and 16 of this invention which regulated Al of this invention. Mg content was 7 ppm of No.15, and 12 ppm of No.16.

Although not shown in the table, microscopic inclusions were observed and analyzed by using an electron microscope and an X-ray analyzer at 10 times at random at 1000 times the field of view according to the cross section of the steel and the comparative steel described above. . As a result, no inclusion of TiN or Ti (C, N) exceeding 3 µm was observed in all test pieces except Comparative Steel No.21.

In addition, as to the fatigue tests conducted, which will be described later steel No.1, No.6, No.15 of the present invention, a 1000-fold line, but the cross-section observation using an electron microscope in 10 fields of view, Al ₂ O ₃ inclusions can be observed There was no.

Table 2 also shows the austenite grain size, tensile strength, internal hardness after nitriding treatment, surface hardness, and residual stress on the surface after nitriding treatment after aging each sample. Here, the code | symbol of the residual stress of Table 2 has shown that + represents tension and-represents compression, and all are compressive residual stress. In addition, in the steel of this invention, Table 3 shows the fatigue test result after aging No.1, 6, 15, the conventional steel No.21, and the comparative steel No.22 at 480 degreeC.

Although the fatigue test has various stress load patterns of rotation bending, tensile compression, and torsion, the maraging steel of the present invention is made of a strip material, and therefore, an evaluation method for loading a bending stress is suitable. Therefore, in the repeated bending fatigue test, it is clear that the conventional maraging steel has a high fatigue strength unless it breaks when high stress is applied to break. Therefore, when repeated bending stress was applied at an average stress of 537 MPa and a maximum stress of 1016 MPa, the fracture was repeated up to 10 ⁷ times.

[Table 1]

TABLE 2

[Table 3]

From Table 2, the maraging steel for metal belts using the maraging steel of this invention is 1700 Mpa or more in tensile strength after ageing, and has sufficient strength as a metal belt use. In particular, in the maraging steel to which Al was positively added, the tensile strength after aging was 1900 Mpa or more. Moreover, it turns out that it has high internal hardness, surface hardness, and large surface compressive residual stress also after nitriding, and it turns out that it has the characteristic equivalent or more even compared with the conventional steel No. 21 containing Ti.

In addition, the inventive steel maintains fine grains having a grain size of ASTM No. 10 or higher due to the effect of adding B.

On the other hand, Comparative Steel No. 22 without Ti and without adding Cr or Al has lower tensile strength after aging, internal hardness after nitriding, surface hardness, and surface compressive residual stress than the steel of the present invention. In addition, since B was not included, the result was that the grains became slightly coarse.

In Table 3, steel Nos. 1 and 6 of the present invention exceed 10 ⁷ times of repeated breaks in the fatigue test results after aging. Moreover, it turns out that steel No. 15 of this invention also has the fatigue characteristic superior to the conventional steel No. 21. Moreover, since the steel of this invention is excellent in nitriding characteristics compared with the conventional steel as mentioned above, the improvement of a fatigue characteristic can be expected further by nitriding treatment.

Thus, the maraging steel for metal belts using the maraging steel of this invention can be made into higher fatigue strength than the conventional maraging steel.

Since the maraging steel of this invention can be used for the metal belt used in severe conditions, it can be applied to the member which requires high tensile strength and high fatigue strength, such as a power transmission metal belt used for the continuously variable transmission for automobiles.

Claims (8)

By mass%
Ni: more than 18.0 and less than 22.0%,
Cr: 0.1-4.0%,
Mo: 3.0-7.0%,
Co: greater than 12.0% and less than 20.0%,
B: greater than 0 and less than 0.01%
Mg: more than 0 and less than 0.005%
≪ / RTI >
Co / 3 + Mo + 4Al: satisfies the relationship of 8.0-15.0%, and also
C, Si, Mn, P, S, Ti, Al, N, O are each
C: 0.008% or less, Si: 0.1% or less, Mn: 0.1% or less, P: 0.01% or less, S: 0.005% or less, Ti: 0.05% or less, Al: 0.05% or less, N: 0.03% or less, O: Regulated in the range of 0.005% or less, and
Al + Ti: 0.07% or less, the remainder being made of Fe and unavoidable impurities. C, Si, Mn, P, S, Ti, Al, N, O in mass%
C: greater than 0 and less than 0.008%, Si: greater than 0 and 0.1% or less, Mn: greater than 0 and 0.1% or less, P: greater than 0 and 0.01% or less, S: greater than 0 and 0.005% or less and Ti: greater than 0 0.05% or less, Al: more than 0, 0.05% or less, N: more than 0, 0.03% or less, O: more than 0, 0.005% or less, maraging steel. The method of claim 1,
Maraging steels with an Mg of 0.0001% to 0.005%. The method of claim 1,
A maraging steel with a mass% of Mo: greater than 5.0% and not more than 7.0% and Co / 3 + Mo + 4Al: 10.0-15.0%. The method of claim 1,
The maraging steel containing Ca: more than 0 and 0.01% or less by mass%. The method according to any one of claims 1 to 5,
Maraging steels having a grain size of 10 or more fine grains in ASTM No. The method of claim 5,
Maraging steel, with a nitride layer formed on its surface. The method of claim 6,
Maraging steel, with a nitride layer formed on its surface.

Images