EP2180073B1 - Acier maraging pour courroie métallique - Google Patents
Acier maraging pour courroie métallique Download PDFInfo
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- EP2180073B1 EP2180073B1 EP07790636.0A EP07790636A EP2180073B1 EP 2180073 B1 EP2180073 B1 EP 2180073B1 EP 07790636 A EP07790636 A EP 07790636A EP 2180073 B1 EP2180073 B1 EP 2180073B1
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- steel
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- maraging steel
- maraging
- strength
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Definitions
- the present invention relates to maraging steel having excellent fatigue strength, and maraging steel for a metallic belt used in continuously variable transmissions for automobiles.
- maraging steel Since maraging steel generally has a very high tensile strength of about 2000 MPa, it has been used for members requiring high strength, such as rocket parts, centrifugal separator parts, aircraft parts, continuously variable transmission parts of automobile engines, and dies in various applications.
- a typical maraging steel has a chemical composition of 18% Ni, 8% Co, 5% Mo, 0.4% Ti, 0.1% Al, and the balance of Fe.
- the maraging steel contains appropriate amounts of Co, Mo and Ti as strengthening elements, and can obtain high strength by precipitating intermetallic compounds such as Ni 3 Mo, Ni 3 Ti, and Fe 2 Mo by aging treatment.
- the fatigue strength especially in a high cycle region is a needed important characteristic, so that it is required to make nonmetallic inclusions such as TiN, which are present in the maraging steel having high strength, fine as far as possible.
- the maraging steel has been used as provided with improved fatigue strength by subjecting it to nitriding treatment to form a nitrided layer on the steel surface.
- an alloy improved to avoid the decrease in fatigue strength occurring with the nonmetallic inclusion being a starting point has been proposed (for example, see following Patent Documents 1 to 3).
- JP-A 2000 345 302 and JP-A 2001 121 710 disclose maraging steels, which do not include Cr and in which the Al content is not reduced.
- US-A 2001 006 081 discloses another related maraging steel with reduced Co content.
- the content of Ti that forms nonmetallic inclusions is reduce to not more than 0.1%. Therefore, although this alloy is advantageous in making TiN, which serves as a start point of fatigue fracture, fine, the alloy has a problem of difficulty in nitriding treatment because it simply restrains the addition of an element forming nonmetallic inclusions.
- the alloy disclosed in JP-A-2001-240943 is advantageous in making TiN, which serves as a start point of fatigue fracture, fine because it contains a reduced amount of Ti. In this alloy, however, it is difficult to ensure a high tensile strength because the content of Co, which is one of the strengthening elements, is kept low.
- Si and Mn are added in order to ensure tensile strength, but the toughness may be decreased by the addition of Si and Mn.
- the alloy disclosed in JP-A-2002-167652 also, is advantageous in making TiN, which serves as a start point of fatigue fracture, fine because it contains a reduced amount of Ti. In this alloy, however, since C is added positively to increase the strength, carbides of Cr, Mo and the like precipitates. Therefore, the fatigue strength may be decreased with the carbides serving as a starting point of fatigue fracture, or the weldability required for continuously variable transmission parts may be deteriorated by the positively added C.
- an object of the present invention is to provide a maraging steel in which the chemical composition thereof can reduce TiN, which serves as a starting point of fatigue fracture in a high cycle region, the surface hardness is increased by facilitating nitriding treatment, the fatigue bending strength is improved by increasing the compression residual stress of a nitrided surface layer, and the former austenitic grains are made fine in order to ensure higher strength and ductility, and a maraging steel for a metallic belt using the aforementioned maraging steel.
- the present inventor found that the decrease in strength caused by the reduction in the Ti content can be compensated while keeping the contents of Ti and N low to reduce TiN, which is an inclusion detrimental for improving the fatigue strength, by increasing the contents of Co and Mo or adding Co and Mo as necessary and increasing the content of Al as well, and further by restricting the value of Co/3 + Mo + 4Al to a proper range. Also, the present inventor found that in order to improve the tensile strength, ductility, and fatigue strength, it is effective to make the grains fine, and this purpose can be attained by the addition of a trace amount of B.
- the present inventor found that in order to solve the difficulty of nitriding treatment caused by the reduction in Ti, the absolute value of the surface compression residual stress caused by nitriding can be increased by the addition of a proper amount of Cr or the addition of proper amounts of Cr and Al, and came at the present invention by keeping the carbon content at an impurity level to ensure the weldability.
- a first type preferable chemical composition has a positively added Al within the range of the above basic chemical composition.
- the maraging steel contains, by mass, 0.1 to 3.0% Cr, and more than 0.15 to not more than 2.5% Al.
- the maraging steel preferably comprises not more than 0.008% C, more than 18.0 to not more than 22.0% Ni, more than 5.0 to not more than 7.0%, and not more than 0.05% Ti, wherein the value of "Co/3 + Mo + 4Al" is 10.0 to 15.0% by mass percent. More preferably, the maraging steel contains, by mass, from more than 12.0% to not more than 20.0% Co.
- a second type preferable chemical composition in accordance with the present invention has a restricted amount of Al and a slightly much amount of Co within the range of the above basic chemical composition.
- the maraging steel contains, by mass, from more than 10.0% to not more than 20.0% Co, not more than 0.05% Ti, and less than 0.1% Al, wherein the value of "Al+Ti" is less than 0.1%.
- the maraging steel may contain, by mass, one or more of not more than 0.01% Ca and not more than 0.005% Mg. It is also noted that the invention maraging steel has a fine grain size of ASTM No. 10 or more.
- the present invention also relates to the above maraging steel for a metallic belt.
- maraging steel it is possible to reduce TiN which may become a starting point of fatigue fracture, and to obtain high strength, surface high hardness after nitriding treatment, and high compression residual stress, so that when the maraging steel is used for a member required to have high fatigue strength, such as a power transmission metallic belt used for a continuously variable transmission of an automobile, industrially remarkable advantages, long durability for fatigue, for example, are obtainable.
- the present invention has been made based on the above-described new knowledge.
- functions of each element contained in the invention maraging steel is described.
- “%" means mass percent.
- C (carbon) forms carbides together with Mo to reduce intermetallic compounds to be precipitated and to decrease the strength. Therefore, the carbon content must be kept low. Also, if carbon is added positively, the danger of deteriorating the weldability required for, for example, continuously variable transmission parts increases. For these reasons, the carbon content is set to be not more than 0.01%. Preferably the carbon content is not more than 0.008%.
- Si is an element capable of making up for the decrease in strength caused by the reduction in Ti by making the intermetallic compounds precipitated during aging treatment or by forming intermetallic compounds together with Ni.
- the Si content since Si may decrease the toughness, in the present invention, the Si content must be kept low to ensure toughness and ductility.
- the addition of Si exceeding 0.1% decreases the toughness and ductility, so that the Si content is set to be not more than 0.1%.
- the preferable range for surely ensuring toughness and ductility is not more than 0.05%.
- Mn is an element capable of making up for the decrease in strength caused by the reduction in Ti because it forms intermetallic compounds together with Ni during aging treatment and contributes to age hardening.
- Mn may decrease the toughness
- the Mn content must be kept low.
- the addition of Mn exceeding 0.1% decreases the toughness and ductility, so that the Mn content is set to be not more than 0.1%.
- the preferable range for surely ensuring toughness and ductility is not more than 0.05%.
- P (phosphorous) and S (sulfur) are detrimental elements that make the maraging steel brittle and decrease the fatigue strength by segregating at the old austenitic grain boundaries or by forming inclusions. Therefore, the P content is set to be not more than 0.01%, and the S content is set to be not more than 0.005%.
- the preferable ranges are not more than 0.005% for P and not more than 0.004% for S.
- Cr is an element that has strong affinity with nitrogen in nitriding, decreases the nitriding depth, increases the nitriding hardness, and increases the compression residual stress of the nitrided surface. Therefore, the addition of Cr is essential. However, the content less than 0.1% does not achieve the effects. On the other hand, even if Cr is added exceeding 4.0%, the effects are not improved further, and the strength after aging decreases greatly. Therefore, the Cr content is set to be 0.1 to 4.0%. When Al is added positively, the sufficient upper limit of Cr content is 3.0%. Ni stably forms a low-C martensitic structure, which is the matrix structure of maraging steel. Therefore, at least 17.0% of Ni must be added.
- the Ni content is set to be 17.0 to 22.0%.
- the preferable Ni range is more than 18.0% and not more than 22.0%.
- Mo is an important element that forms fine intermetallic compounds such as Ni 3 Mo and Fe 2 Mo during aging treatment and contributes to precipitation strengthening. Also, Mo is an effective element for increasing the surface hardness and compression residual stress caused by nitriding. If the Mo content is less than 3.0%, the tensile strength is insufficient, and on the other hand, if it is more than 7.0%, coarse intermetallic compounds, in which Fe and Mo are the principal elements, become liable to be formed. Therefore, the Mo content is set to be 3.0 to 7.0%.
- the preferable Mo range is more than 5.0% and not more than 7.0%.
- Co is an element that increases the degree of solid solution of the aging precipitate forming elements such as Mo and Al at the solid solution heat treatment temperature without exerting a great influence on the stability of the martensitic structure of matrix, promotes precipitation of fine intermetallic compounds containing Mo and Al by decreasing the degree of solid solution of Mo and Al in the aging precipitation temperature region, and contributes to aging precipitation strengthening. Therefore, much Co must be added from the viewpoint of strength and toughness. If the Co content is not more than 7.0%, the maraging steel in which Si, Mn and Ti are reduced has difficulty in obtaining sufficient strength. On the other hand, if the Co content exceeds 20.0%, austenite is made stable and it is difficult to obtain martensitic structure.
- the Co content is set to be more than 7.0% and not more than 20.0%.
- the preferable Co range is more than 12.0% and not more than 20.0%.
- the Co content should be made slightly high. Therefore, the Co range is made more than 10.0% and not more than 20.0%.
- Ti is inherently one of the important strengthening elements in the maraging steel, but at the same time, is a detrimental element that forms TiN or Ti(C,N), which is an inclusion, and thereby decreases the fatigue strength especially in the super-high cycle region. Therefore, when importance is attached to fatigue strength, the Ti content must be kept low as an impurity. Also, Ti easily forms a thin and stable oxide film on the surface, and the formation of this oxide film hinders nitriding reaction, so that it is difficult to obtain a sufficient compression residual stress on the nitrided surface. To perform nitriding easily or to increase the compression residual stress on the nitrided surface, the content of Ti, which is a detrimental impurity element, must be kept low.
- the Ti content is set to be not more than 0.1%.
- the Ti content should be not more than 0.05%, and further preferably not more than 0.01%.
- Al is an element that is usually added in small amounts for deoxidation, and forms intermetallic compounds together with Ni during aging treatment to contribute to strengthening.
- Si, Mn and Ti are reduced, it is preferred that the strength be increased by the addition of Al.
- Al must be added to facilitate the nitriding treatment in the maraging steel in which Ti is reduced to obtain a good nitrided layer, as well.
- the Al content is not more than 0.15%, sufficient strengthening action due to aging treatment cannot be accomplished.
- the Al content is more than 2.5%, much Aln and Al 2 O 3 inclusions are formed to decrease the fatigue strength, or a thin and stable oxide film is formed on the surface to hinder nitriding reaction. Therefore, the Al content is set to be more than 0.15% and not more than 2.5%.
- the preferable upper limit at the time when Al is added positively is made 1.5%.
- the Al content is restricted, the nonmetallic inclusions in the maraging steel can be reduced. Also, to easily keep smooth the surface roughness of the maraging steel on account of Al, the starting point of fatigue fracture is reduced, and when importance is attached to fatigue strength, Al should be restricted.
- the preferable Al content in the case where Al is restricted is described below. Al forms nonmetallic inclusions by combining with oxygen and nitrogen, and may decrease the fatigue strength, so that when importance is attached to fatigue strength, the Al content should be kept low. If the Al content is 0.1% or more, AlN and Al 2 O 3 inclusions are formed easily, and thereby the fatigue strength may be decreased. Therefore, the Al content should be restricted to less than 0.1%.
- the Al range is not more than 0.05%.
- Al and Ti are elements that form nonmetallic inclusions, keeping the total amount of Al and Ti low is effective in improving the fatigue strength, so that the content of "Al+Ti" is made not more than 0.1%.
- the preferable range of "Al+Ti" is not more than 0.07%.
- All of Co, Mo and Ti are main strengthening elements in the maraging steel, and Al also is an element contributing to aging strengthening of the maraging steel. If the Ti content is kept low, when the contents of Co and Mo are increased or Al is added positively, it is necessary to make up for the decrease in strength on account of Ti by increasing the content of Al in addition to Co and Mo. However, the contributions of the elements to the strengthening are not the same, and the magnitudes of strengthening due to Co and Al are 1/3 times and four times the magnitude of strengthening due to Mo, respectively. Therefore, the strengthening due to Co, Mn and Al can be expressed by Co/3 + Mo + 4Al. If the value of Co/3 + Mo + 4Al is less than 8.0% by mass percent, the strength is insufficient.
- the value of Co/3 + Mo + 4Al is set to be 8.0 to 15.0%.
- the preferable range of Co/3 + Mo + 4Al is 10.0 to 15.0%.
- N nitrogen
- the N content is an impurity element that forms an inclusion of TiN or Ti(C,N) by combining with Ti to decrease the fatigue strength especially in a super-high cycle region.
- the N content In the maraging steel containing Ti, to prevent the formation of coarse TiN or Ti(C,N), the N content must be kept significantly low. However, in the maraging steel scarcely containing Ti, even the amount of N mixed in on account of usual vacuum melting exerts a little adverse influence, so that the N content is set to be not more than 0.03%. Desirably, the N content should be not more than 0.01%. Further desirably, the N content should be not more than 0.005%.
- ⁇ (oxygen) is an impurity element that forms oxide-based inclusions to decrease the toughness and fatigue strength. Therefore, the O content was restricted to not more than 0.005%. Desirably, the O content should be not more than 0.003%.
- B (boron) is an element that makes fine the old austenitic grains at the time when solid solution heat treatment is performed after cold working to contribute to the strengthening, and has an effect of restraining surface roughness, therefore being added indispensably. If the B content is more than 0.01%, the toughness decreases, so that the B content is set to be not more than 0.01% (excluding 0%). Desirably, the B content should be not more than 0.005% (excluding 0%).
- the preferable lower limit of the content of B capable of surely making the old austenitic grains fine is 0.0002%, and the further preferable lower limit thereof is 0.0003%.
- the present invention steel may contain not more than 0.01% Ca and/or not more than 0.005% Mg.
- the ingot thereof can be manufactured by vacuum induction melting or melting in a vacuum atmosphere, for example, by further performing vacuum arc remelting or electroslag remelting after the vacuum induction melting.
- vacuum induction melting or melting in a vacuum atmosphere for example, by further performing vacuum arc remelting or electroslag remelting after the vacuum induction melting.
- It Al is added positively in order to improve the strength in some cases, there is a concern about occurrence of coarse and hard Al 2 O 3 inclusions having a size exceeding, for example, 25 ⁇ m, or a concern about occurrence of cluster Al 2 O 3 .
- the Al 2 O 3 inclusions have high hardness and high melting point, and are scarcely deformed, for example, even during hot plastic working. Therefore, there is a possibility of producing a surface defect on the maraging steel for a metallic belt due to the occurrence of a flaw on a roll, for example, during cold rolling. For this reason, the Al 2 O 3 inclusions should be made composite inclusions combined with other oxides to decrease the hardness or to lower the melting point. Also, preferably, an element capable of preventing occurrence of cluster Al 2 O 3 is added in order to prevent inclusion defects.
- Si, Mn, Ca and Mg can be raised.
- the amounts of addition of Si and Mn are restricted as elements that reduce the toughness and ductility. Therefore, preferably by adding one or more of Ca and Mg other than Si and Mn, Al 2 O 3 inclusions are made to be composite inclusions.
- Ca and Mg have an effect of preventing occurrence of cluster Al 2 O 3 . Therefore, in the present invention steel, not more than 0.01% Ca and/or not more than 0.005% Mg are added. To surely achieve the effects of Ca and Mg, the lower limit of content should be 0.001% for Ca and 0.0001% for Mg.
- the elements other than explained above are made Fe and unavoidable impurities. The following element may be added for the purpose of deoxidation, desulfurization, and the like in the following range: Zr ⁇ 0.01 %
- the old austenitic grains (herein, in the case of maraging steel, grains mean the old austenitic grains) can be so fine as correspond to ASTM No. 10 or more by solid solution heat treatment performed at a proper temperature corresponding to the composition, for example, at a temperature of about 780 to 1000°C after cold working of not less than 10%.
- maraging steel not more than 2.5% of Al is contained as mentioned above.
- Concerning the maraging steel of the present invention there was obtained a new knowledge that a characteristic phenomenon that the surface shape of maraging steel becomes rough according to the Al content occurs. It is presumed that the cause for this phenomenon is that Al having a high diffusion coefficient concentrates on the surface due to high-temperature heat treatment such as solid solution heat treatment and the atmosphere thereof, whereby surface oxidation is brought about. If a surface state becomes rough, for example, in the case where the maraging steel of the present invention is used for a power transmission metallic belt used for a continuously variable transmission of an automobile, the risk of fatigue fracture in the low cycle side becomes great. Therefore, the surface shape should be kept smooth as far as possible by Al.
- the atmosphere of solid solution heat treatment performed especially during cold working should be adjusted to the atmosphere of oxygen or nitrogen that is difficult to form oxides or nitrides by combining with Al.
- a vacuum atmosphere, hydrogen atmosphere, or argon atmosphere should be used.
- the hydrogen atmosphere and the argon atmosphere which are capable of continuously treating cold rolled materials, are favorable from the viewpoint of productivity.
- hydrogen is preferably used because of being inexpensive.
- the invention maraging steel scarcely contain Ti that forms a stable oxide film having a possibility of hindering nitriding. Therefore, various types of nitriding treatment such as usual gas nitriding, gas nitrocarburizing, nitrosulfurizing, ion nitriding, and salt bath nitriding can be performed easily. Also, for the invention maraging steel for a metallic belt, which contains no Ti, regarding the absolute value of compression residual stress of the nitrided layer liable to decrease, as well, the absolute value of compression residual stress of the nitrided layer can be increased by Cr and Al that have an effect of enhancing the nitriding hardness and the absolute value of compression residual stress of the nitrided layer.
- the maraging steel in which the chemical composition thereof is adjusted to the above-described range specified in the present invention is formed into a strip shape having a thickness of, for example, 0.05 mm or smaller to be used for a steel strip of maraging steel for a metallic belt, and nitriding treatment is performed under the conditions suitable for the steel strip of maraging steel for a metallic belt.
- a thin nitrided layer having a thickness of about 20 to 40 ⁇ m can be formed on the surface with nitrides being scarcely formed, and a high compression residual stress can be given to the surface, so that the improvement in fatigue characteristics can be expected.
- the maraging steel for a metallic belt of the present invention has a high tensile strength and high fatigue strength, and can be nitrided easily, so that this maraging steel is suitable for a metallic belt for a continuously variable transmission of an automobile engine.
- the present invention will be explained in more detail with reference to the following Example.
- the invention maraging steel and a comparative steel were melted in a vacuum induction melting furnace to produce ingots of 10 kg, and the ingots were subjected to homogenizing, and then were hot forged. Further, steel strips each having a thickness of about 0.3 mm were produced by hot rolling and cold rolling, whereby maraging steels for a metallic belt were produced. Thereafter, solid solution heat treatment was performed at 820 to 900°C, and further aging treatment was performed at 490°C. Subsequently, gas nitrocarburizing was performed under the condition that the nitride depth is 20 to 40 ⁇ m at 450 to 470°C. The solid solution heat treatment was performed in a hydrogen atmosphere.
- Figs. 1 and 2 are electron microphotographs of the surface of steel strips each having a thickness of 0.3 mm of the invention steel Nos. 6 and 15, respectively.
- Fig. 1 shows a maraging steel in which Al is added positively.
- Fig. 2 shows a maraging steel in which the addition of Al is restricted. For this maraging steel, it is found that the surface shape is smooth.
- Table 1 shows the chemical compositions of maraging steel Nos. 1 to 8 (with positively added Al), the invention maraging steel Nos. 11 to 16 (with restricted amounts of Al), and conventional steel and comparative steel Nos. 21 and 22, respectively.
- Comparative steel No. 21 is a conventional steel containing Ti
- comparative steel No. 22 is a maraging steel in which Ti is not contained, and Al is not added.
- the carbon content was adjusted to the range of not more than 0.01% to prevent the deterioration in weldability.
- Mg was added in steel Nos. 5 and 6 in which Al was added positively.
- the Mg content was 10 ppm for No. 5 and 6 ppm for No. 6.
- Table 2 shows old austenitic grain size numbers and tensile strength after aging of specimen, internal hardness and surface hardness after nitriding treatment, and surface residual stress after gas nitrocarburizing.
- the symbol "+” of residual stress represents tension, and the symbol “-” thereof represents compression. All of the residual stresses are compression residual stresses.
- Table 3 shows the results of fatigue tests after aging at 480°C conducted on the steel Nos. 1, 6 and 15, conventional steel No. 21, and comparative steel No. 22.
- various stress applying modes such as rotational bending, tension/compression, and torsion can be used. Since the invention maraging steel is used as a strip material, an evaluation method in which bending stress is applied is suitable.
- Table 2 indicates that all of the maraging steels for a metallic belt using the maraging steels of the present invention have a tensile strength after aging of 1700 MPa or higher, having a sufficient strength of a metallic belt.
- the maraging steels have high internal hardness, surface hardness, and surface compression residual stress, and that they have characteristics equivalent to or higher than those of conventional steel No. 21 containing Ti.
- invention steels has the austenitic grain size so fine as correspond to ASTM No. 10 or more due to the effect of adding B.
- the maraging steel for a metallic belt using the maraging steel of the present invention can be provided with a fatigue strength higher than that of the conventional maraging steel.
- the maraging steel in accordance with the present invention can be used for a metallic belt used under stringent conditions, and therefore can be used for members requiring high tensile strength and high fatigue strength, such as a power transmission metallic belt used for an automotive continuously variable transmission and the like.
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Claims (7)
- Acier maraging constitué de, en pour cent en masse,
pas plus de 0,01 % de C,
pas plus de 0,1 % de Si,
pas plus de 0,1 % % de Mn,
pas plus de 0,01 % de P,
pas plus de 0,005 % de S,
17,0 à 22,0 % de Ni,
0,1 à 4,0 % de Cr,
3,0 à 7,0 % de Mo,
plus de 10,0 % et pas plus de 20,0 % de Co, pas plus de 0,1 % de Ti,
pas plus de 0, 05 % d'Al,
pas plus de 0,03 % de N,
pas plus de 0,005 % d'O, et
pas plus de 0,01 % de B (à l'exclusion de zéro %) ; et,
optionnellement, pas plus de 0,01 % de Ca, optionnellement, pas plus de 0,005 % de Mg, et,
optionnellement, pas plus de 0,01 % de Zr, et
le reste étant constitué de Fe et d'impuretés inévitables,
dans lequel la valeur de « Co/3 + Mo + 4Al » est de 8,0 à 15,0 % en pour cent en masse. - Acier maraging selon la revendication 1, dans lequel la teneur en carbone n'excède pas 0,008 % en masse, la teneur en Ni n'excède pas 18,0 % et n'excède pas 22,0 % en masse, la teneur en Mo n'excède pas 5,0 % et n'excède pas 7,0 % en masse, et la teneur en Ti n'excède pas 0,05 % en masse, dans lequel Co/3 + Mo + 4Al vaut 10,0 à 15,0 % en pour cent en masse.
- Acier maraging selon la revendication 1 ou 2, dans lequel la teneur en Co n'excède pas 12,0 % et n'excède pas 20,0 % en masse.
- Acier maraging ayant une résistance élevée à la fatigue selon la revendication 1, dans lequel la teneur en Ti n'excède pas 0,05 % en masse, dans lequel la valeur de « Al+Ti » est inférieure à 0,1 % en masse.
- Acier maraging ayant une résistance élevée à la fatigue selon la revendication 4, dans lequel la valeur de « Al+Ti » n'excède pas 0, 07 % en masse.
- Acier maraging selon l'une quelconque des revendications 1 à 5, qui a une taille de grains fine de N° 10 ou plus selon la norme ASTM.
- Acier maraging destiné à une courroie métallique faite de l'acier maraging tel que défini dans l'une quelconque des revendications 1 à 6.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP2007/063832 WO2009008071A1 (fr) | 2007-07-11 | 2007-07-11 | Acier vieilli thermiquement et acier vieilli thermiquement pour courroie métallique |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2180073A1 EP2180073A1 (fr) | 2010-04-28 |
EP2180073A4 EP2180073A4 (fr) | 2011-04-06 |
EP2180073B1 true EP2180073B1 (fr) | 2013-09-11 |
Family
ID=40228268
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP07790636.0A Revoked EP2180073B1 (fr) | 2007-07-11 | 2007-07-11 | Acier maraging pour courroie métallique |
Country Status (5)
Country | Link |
---|---|
US (1) | US20100189590A1 (fr) |
EP (1) | EP2180073B1 (fr) |
KR (2) | KR20100011991A (fr) |
CN (1) | CN101688271B (fr) |
WO (1) | WO2009008071A1 (fr) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016170397A1 (fr) | 2015-04-23 | 2016-10-27 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
WO2017064537A1 (fr) | 2015-10-15 | 2017-04-20 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
MX2011009958A (es) * | 2009-03-26 | 2011-10-06 | Hitachi Metals Ltd | Tira de acero al niquel con muy bajo contenido en carbono. |
CN103339267B (zh) * | 2010-12-20 | 2016-03-09 | 罗伯特·博世有限公司 | 用于传动带金属环构件的生产方法的热处理方法 |
WO2013047078A1 (fr) | 2011-09-30 | 2013-04-04 | 日立金属株式会社 | Acier vieilli thermiquement |
CN104259240B (zh) * | 2014-09-12 | 2016-03-09 | 攀钢集团江油长城特殊钢有限公司 | 一种18Ni-200钢棒及其制备方法 |
JP6202034B2 (ja) | 2015-04-06 | 2017-09-27 | トヨタ自動車株式会社 | 金属リング及びその製造方法 |
NL1043487B1 (en) * | 2019-11-28 | 2021-08-31 | Bosch Gmbh Robert | Ring component of a drive belt for a continuously variable transmission |
SE544681C2 (en) * | 2020-11-05 | 2022-10-18 | Uddeholms Ab | Maraging steel for hot-work tools |
CN114908300A (zh) * | 2021-02-10 | 2022-08-16 | 华为技术有限公司 | 钢材料、钢结构件及其制备方法和终端 |
Family Cites Families (16)
Publication number | Priority date | Publication date | Assignee | Title |
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GB1104932A (en) * | 1965-06-18 | 1968-03-06 | Wilkinson Sword Ltd | Improvements in or relating to safety razor blades |
US3341372A (en) * | 1965-07-12 | 1967-09-12 | Int Nickel Co | Process for heat treating cast maraging steels |
JPH01142052A (ja) * | 1987-11-27 | 1989-06-02 | Sumitomo Metal Ind Ltd | 継目無金属ベルト及びその製造方法 |
FI84369C (fi) * | 1988-10-11 | 1991-11-25 | Rauma Repola Oy | Maraging-staol. |
JP2909089B2 (ja) * | 1989-04-26 | 1999-06-23 | 日立金属株式会社 | マルエージング鋼およびその製造方法 |
JPH10152759A (ja) * | 1996-11-21 | 1998-06-09 | Daido Steel Co Ltd | 靱性に優れたマルエージング鋼 |
KR100374980B1 (ko) * | 1999-02-12 | 2003-03-06 | 히다찌긴조꾸가부시끼가이사 | 우수한 기계가공성을 갖는 다이스용 고장력강 |
JP4178490B2 (ja) * | 1999-06-08 | 2008-11-12 | 日立金属株式会社 | 高疲労強度を有するマルエージング鋼ならびにそれを用いたマルエージング鋼帯 |
JP3503815B2 (ja) * | 1999-10-28 | 2004-03-08 | 日立金属株式会社 | 固溶化処理時の表面肌荒れを抑制した金属ベルト用鋼帯 |
JP4427772B2 (ja) | 1999-12-24 | 2010-03-10 | 日立金属株式会社 | 高疲労強度を有するマルエージング鋼ならびにそれを用いたマルエージング鋼帯 |
EP1111080B1 (fr) * | 1999-12-24 | 2007-03-07 | Hitachi Metals, Ltd. | Acier maraging à haute résistance à la fatigue et bandes en cet acier maraging |
FR2816959B1 (fr) * | 2000-11-17 | 2003-08-01 | Imphy Ugine Precision | Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid |
JP2002161308A (ja) * | 2000-11-24 | 2002-06-04 | Daido Steel Co Ltd | 高強度、高耐疲労構造用鋼の製造方法 |
JP2002167652A (ja) | 2000-11-28 | 2002-06-11 | Daido Steel Co Ltd | 高強度・高耐疲労特性に優れた薄板材 |
JP2002285290A (ja) * | 2001-03-27 | 2002-10-03 | Daido Steel Co Ltd | 高強度・高耐疲労構造用鋼及びその製造方法 |
JP5046363B2 (ja) * | 2005-12-13 | 2012-10-10 | 日立金属株式会社 | 高疲労強度を有する動力伝達用ベルト用マルエージング鋼ならびにそれを用いた動力伝達用ベルト用マルエージング鋼帯 |
-
2007
- 2007-07-11 KR KR1020097027091A patent/KR20100011991A/ko active Search and Examination
- 2007-07-11 KR KR1020127017064A patent/KR20120078757A/ko not_active Application Discontinuation
- 2007-07-11 EP EP07790636.0A patent/EP2180073B1/fr not_active Revoked
- 2007-07-11 US US12/668,583 patent/US20100189590A1/en not_active Abandoned
- 2007-07-11 CN CN2007800537486A patent/CN101688271B/zh active Active
- 2007-07-11 WO PCT/JP2007/063832 patent/WO2009008071A1/fr active Application Filing
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016170397A1 (fr) | 2015-04-23 | 2016-10-27 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
WO2016170519A1 (fr) | 2015-04-23 | 2016-10-27 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
US11186886B2 (en) | 2015-04-23 | 2021-11-30 | Aperam | Steel, product made of said steel, and manufacturing method thereof |
WO2017064537A1 (fr) | 2015-10-15 | 2017-04-20 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
WO2017064684A1 (fr) | 2015-10-15 | 2017-04-20 | Aperam | Acier, produit réalisé en cet acier, et son procédé de fabrication |
CN108138286A (zh) * | 2015-10-15 | 2018-06-08 | 艾普伦 | 钢、所述钢制造的产品及其制造方法 |
US10731231B2 (en) | 2015-10-15 | 2020-08-04 | Aperam | Steel, product created from said steel, and manufacturing method thereof |
Also Published As
Publication number | Publication date |
---|---|
KR20120078757A (ko) | 2012-07-10 |
KR20100011991A (ko) | 2010-02-03 |
WO2009008071A1 (fr) | 2009-01-15 |
CN101688271A (zh) | 2010-03-31 |
US20100189590A1 (en) | 2010-07-29 |
CN101688271B (zh) | 2013-03-27 |
EP2180073A4 (fr) | 2011-04-06 |
EP2180073A1 (fr) | 2010-04-28 |
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