EP3263721B1 - High temperature wear-resistant aluminum-bronze-based material - Google Patents

High temperature wear-resistant aluminum-bronze-based material Download PDF

Info

Publication number
EP3263721B1
EP3263721B1 EP16755004.5A EP16755004A EP3263721B1 EP 3263721 B1 EP3263721 B1 EP 3263721B1 EP 16755004 A EP16755004 A EP 16755004A EP 3263721 B1 EP3263721 B1 EP 3263721B1
Authority
EP
European Patent Office
Prior art keywords
mass
bronze
less
high temperature
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP16755004.5A
Other languages
German (de)
French (fr)
Other versions
EP3263721A4 (en
EP3263721A1 (en
Inventor
Takashi Murakami
Hajime Nakayama
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sankyo Oilless Industries Inc
Original Assignee
Sankyo Oilless Industries Inc
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sankyo Oilless Industries Inc filed Critical Sankyo Oilless Industries Inc
Publication of EP3263721A1 publication Critical patent/EP3263721A1/en
Publication of EP3263721A4 publication Critical patent/EP3263721A4/en
Application granted granted Critical
Publication of EP3263721B1 publication Critical patent/EP3263721B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/01—Alloys based on copper with aluminium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
    • B22D27/20—Measures not previously mentioned for influencing the grain structure or texture; Selection of compositions therefor
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/05—Alloys based on copper with manganese as the next major constituent

Definitions

  • the present invention relates to an aluminum-bronze-based material having high wear resistance in high-temperature environments.
  • copper alloys such as high-strength brass castings are generally used in sliding members such as exhaust valve bushes.
  • Patent Literature 1 discloses a copper-based bearing sliding material which contains 3 to 15% by mass of Al, 1 to 8% by mass of Mn, 0.05 to 5% by mass of Si, 0.5 to 5% by mass of Ni, and 1 to 10% by mass of Fe, with the remainder being unavoidable impurities and Cu, in which an Fe-Mn-Si-based hard material is dispersed.
  • Patent Literature 2 discloses a copper-based alloy containing 6.5 to 10% by mass Al, 6.0 to 12.0% by mass Mn, 1.5 to 2.5% by mass Fe, 0.8 to 2.5% by mass Si, 0.4 to 1.5% by mass Co and 1.0 to 2.0% by mass Ni.
  • Patent Literature 1 the hardness of the matrix material of the known aluminum bronze-based sliding member as disclosed in Patent Literature 1 decreases in high-temperature environments (for example, a high-temperature environment at 150°C to 350°C). Accordingly, the allowable surface pressure value is lowered, and it cannot be said that wear resistance is sufficient. Thus, a further sophisticated material is demanded to be supplied in order to reduce the replacement frequency of sliding members in industrial machines which are used in adverse environments where the replacement is not easy.
  • the present invention has been made to solve such a known problem, and an object thereof is to provide a material which has both surface pressure resistance and wear resistance not only in normal temperature environments but also in high-temperature environments.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present invention is characterized in that an Al content is 9.0% by mass or more and 11.0% by mass or less, an Ni content is 1.0% by mass or more and 3.0% by mass or less, an Mn content is 8.5% by mass or more and 15.0% by mass or less, an Si content is 2.0% by mass or more and 4.0% by mass or less, an Fe content is 0.5% by mass or more and 5.0% by mass or less, and a Co content is 0.01% by mass or more and 1.5% by mass or less, with the remainder being substantially Cu.
  • a sliding member which has both surface pressure resistance and wear resistance even in high-temperature environments.
  • the reduction of the wear amount due to sliding movements enables the replacement frequency of a component such as a sliding member to be drastically reduced in industrial machines and molds of which sliding members are not easy to replace.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment is a material which contains Al, Ni, Mn, Si, Fe, and Co in respective predetermined amounts in terms of % by mass, with the remainder being Cu.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Al content of 9.0% by mass or more and 11.0% by mass or less, and preferably 9.0% by mass or more and 10.0% by mass or less.
  • the matrix material can have an appropriate hardness of HV280 or more, thereby improving surface pressure resistance. It is noted that the hardness of the matrix material is measured by a method in accordance with JIS Z2243 2008.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Ni content of 1.0% by mass or more and 3.0% by mass or less, and preferably 1.5% by mass or more and 2.5% by mass or less.
  • Ni enables the solubility limit of Al in an ⁇ phase to be widened, and also the melting point of the matrix material to be increased thereby improving heat resistance.
  • the inclusion of Ni contributes to deposition of a hard material, together with Fe-Si-Mn described later.
  • the heat resistance of the matrix material is not satisfied.
  • the Ni content exceeds the above-described value range, there is the drawback that the matrix material is embrittled, and a manufactured product becomes expensive because Ni is a rare metal.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has a structure in which an Fe-Mn-Si-based hard material is dispersed, the wear resistance as a sliding member improves.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Mn content of 8.5% by mass or more and 15.0% by mass or less, preferably 8.5% by mass or more and 13.0% by mass or less, and more preferably 8.5% by mass or more and 10.0% by mass or less.
  • Mn content is within the above-described value range
  • Si, Mn and the like described later causes an Fe-Si-Mn-based hard material to be deposited in the matrix material, thereby improving wear resistance.
  • the matrix material can have suitable toughness.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Fe content of 0.5% by mass or more and 5.0% by mass or less, preferably 1.0% by mass or more and 5.0% by mass or less, and more preferably 1.5% by mass or more and 5.0% by mass or less.
  • Fe content is within the above-described value range, Fe is deposited together with Mn-Si and the like as a hard material in the matrix material, and particularly contributes to a finer structure of the above-described hard material, thereby improving the properties as a sliding member.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Si content of 2.0% by mass or more and 4.0% by mass or less, preferably 2.0% by mass or more and 3.0% by mass or less, and more preferably 2.5% by mass or more and 3.0% by mass or less.
  • Si content is within the above-described value range, Si, together with Mn and Fe, causes a eutectic hard material to be deposited, thereby improving sliding properties.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has a Co content of 0.01% by mass or more and 1.5% by mass or less. According to the present embodiment, the inclusion of Co improves heat resistance.
  • FIGs. 1 to 4 are each a diagram illustrating a configuration of a sliding member which adopts as a base material the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment.
  • FIG. 1 illustrates a plate-like sliding member 1 which is the type having no solid lubricant.
  • FIG. 2 illustrates a plate-like sliding member 2 which is the type having a plurality of pieces of a solid lubricant 3 embedded therein.
  • FIG. 3 illustrates a hollow cylindrical sliding member 4 which is the type having no solid lubricant.
  • FIG. 4 illustrates a hollow cylindrical sliding member 5 which is the type having a plurality of pieces of a solid lubricant 6 embedded therein. It is noted that FIGs. 1 to 4 illustrate examples of the form of a sliding member, and the form of the sliding member is not limited to these embodiments .
  • a plurality of pieces of a solid lubricant having a self-lubricating action may be embedded in portions of a sliding surface formed from the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment.
  • the solid lubricant according to the present embodiment to be used may include solid lubricants, such as a graphite-based solid lubricant, a PTFE-based solid lubricant, a MoS2-based solid lubricant, and a Pb alloy-based solid lubricant.
  • the provision of the sliding surface in which a solid lubricant is embedded causes the lubricant to be dispersed on the sliding surface even in high-temperature environments. Therefore, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment can have improved sliding properties, and becomes suitable as a sliding member.
  • the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment have a Vickers hardness of HV280 or more, an elongation of 0.5% or more, and a tensile strength of 500 N/mm 2 or more.
  • HV280 Vickers hardness of HV280 or more
  • elongation 0.5% or more
  • tensile strength 500 N/mm 2 or more.
  • the elongation refers to an elongation that is measured with a tensile test piece in accordance with JIS Z2241. Also, when the tensile strength is equal to or more than 500 N/mm 2 or more, load bearing properties in high-temperature environments are improved.
  • the sliding properties of the present invention will be described in detail by way of examples.
  • Table 1 indicates composition values [Wt%] of the test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5. The composition values were obtained by ICP emission spectrochemical analysis.
  • the test pieces according to Example 1 to Example 8 have a composition in which an Al content was 9.0% by mass or more and 11.0% by mass or less, an Mn content was 8.5% by mass or more and 15.0% by mass or less, an Fe content was 0.5% by mass or more and 5.0% by mass or less, an Ni content was 1.0% by mass or more and 3.0% by mass or less, an Si content was 2.0% by mass or more and 4.0% by mass or less, and a Co content was 0.01% by mass or more and 1.5% by mass or less, with the remainder being substantially Cu.
  • composition of part of the metals contained in each of Comparative Example 1 to Comparative Example 5 is outside the range of the above-described examples.
  • Table 1 (all examples except example 3 outside claimed range) Cu Al Ni Mn Si Fe Co Example 1 Remainder 9.37 1.87 14.80 2.86 4.90 1.00
  • Example 2 Remainder 9.22 2.01 8.73 2.95 1.68 1.06
  • Example 3 Remainder 9.38 1.73 9.06 3.32 1.16 0.27
  • Example 4 Remainder 9.33 1.97 14.30 2.86 1.67 1.02
  • Table 2 indicates measurement results of the hardness and wear amount for the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5.
  • Table 2 (all examples except example 3 outside claimed range) Hardness [HV] Wear amount [ ⁇ m] Example 1 372 42.8 Example 2 341 42.5 Example 3 334 42.3 Example 4 362 40.8 Example 5 302 40.5 Example 6 306 36.5 Example 7 342 35.5 Example 8 289 35.5 Comparative Example 1 181 48.0 Comparative Example 2 321 53.8 Comparative Example 3 334 51.5 Comparative Example 4 297 58.8 Comparative Example 5 410 49.8
  • the hardness was obtained by measuring the Vickers hardness of the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5 at room temperature. As understood from Table 2, the hardness of the test pieces according to Examples 1 to 8 is 280 or more.
  • the wear amount was measured by performing a block-on-ring type sliding test for the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5.
  • the condition of the sliding test is a surface pressure of 10 MPa, a sliding speed of 10 m/min, an environment temperature of 250°C, and a sliding distance of 500 m.
  • the sliding test was performed with a dedicated test machine.
  • the block test piece was pressed against a ring test piece in a state where the temperature in the test machine was maintained at 250°C thereby to apply a load, and the ring test piece was rotated at a constant speed. It is noted that S45C (quenched and tempered at high frequency) was used as the ring test piece that is a mating material.
  • the wear amount of the block test pieces according to Examples 1 to 8 is 35.5 ⁇ m or more and 42.8 ⁇ m or less, indicating that the wear amount is small.
  • the wear amount of the block test pieces according to Comparative Examples 1 to 5 is 48.0 ⁇ m or more and 58.8 ⁇ m or less, indicating that the wear amount is large.
  • the wear amount is 40.8 ⁇ m or less in Example 4 to Example 8. Therefore, it is understood that these compositions are preferable. Furthermore, the wear amount is 36.5 ⁇ m or less in Example 6 to Example 8. Therefore, it is understood that these compositions are more preferable.
  • a sliding member which has both surface pressure resistance and wear resistance even in high-temperature environments. Furthermore, by reducing the wear amount of the sliding member, the replacement frequency of the sliding member can be drastically reduced in industrial machines of which the sliding members are not easy to replace.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)

Description

    Technical Field
  • The present invention relates to an aluminum-bronze-based material having high wear resistance in high-temperature environments.
    • Background Art
  • In high-temperature environments in industrial machines and facilities such as incinerators, copper alloys such as high-strength brass castings are generally used in sliding members such as exhaust valve bushes.
  • As an example of such a sliding member, Patent Literature 1 discloses a copper-based bearing sliding material which contains 3 to 15% by mass of Al, 1 to 8% by mass of Mn, 0.05 to 5% by mass of Si, 0.5 to 5% by mass of Ni, and 1 to 10% by mass of Fe, with the remainder being unavoidable impurities and Cu, in which an Fe-Mn-Si-based hard material is dispersed.
  • Patent Literature 2 discloses a copper-based alloy containing 6.5 to 10% by mass Al, 6.0 to 12.0% by mass Mn, 1.5 to 2.5% by mass Fe, 0.8 to 2.5% by mass Si, 0.4 to 1.5% by mass Co and 1.0 to 2.0% by mass Ni.
    • Citation List Patent Literature
    • Patent Literature 1: JP3929288E
    • Patent Literature 2: JPS62235446A
    Summary of Invention Technical Problem
  • However, the hardness of the matrix material of the known aluminum bronze-based sliding member as disclosed in Patent Literature 1 decreases in high-temperature environments (for example, a high-temperature environment at 150°C to 350°C). Accordingly, the allowable surface pressure value is lowered, and it cannot be said that wear resistance is sufficient. Thus, a further sophisticated material is demanded to be supplied in order to reduce the replacement frequency of sliding members in industrial machines which are used in adverse environments where the replacement is not easy.
  • The present invention has been made to solve such a known problem, and an object thereof is to provide a material which has both surface pressure resistance and wear resistance not only in normal temperature environments but also in high-temperature environments. Solution to Problem
  • The high temperature wear-resistant aluminum-bronze-based material according to the present invention is characterized in that an Al content is 9.0% by mass or more and 11.0% by mass or less, an Ni content is 1.0% by mass or more and 3.0% by mass or less, an Mn content is 8.5% by mass or more and 15.0% by mass or less, an Si content is 2.0% by mass or more and 4.0% by mass or less, an Fe content is 0.5% by mass or more and 5.0% by mass or less, and a Co content is 0.01% by mass or more and 1.5% by mass or less, with the remainder being substantially Cu. Advantageous Effects of Invention
  • According to the high temperature wear-resistant aluminum-bronze-based material according to the present invention, there can be provided a sliding member which has both surface pressure resistance and wear resistance even in high-temperature environments. The reduction of the wear amount due to sliding movements enables the replacement frequency of a component such as a sliding member to be drastically reduced in industrial machines and molds of which sliding members are not easy to replace.
    • Brief Description of Drawings
    • FIG. 1 is a schematic diagram of a plate-like sliding member which adopts as a base material a high temperature wear-resistant aluminum-bronze-based material according to the present embodiment and which is the type having no solid lubricant.
    • FIG. 2 is a schematic diagram of a plate-like sliding member which adopts as a base material the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment and which is the type having a solid lubricant.
    • FIG. 3 is a schematic diagram of a hollow cylindrical sliding member which adopts as a base material a high temperature wear-resistant aluminum-bronze-based material according to the present embodiment and which is the type having no solid lubricant.
    • FIG. 4 is a schematic diagram of a hollow cylindrical sliding member which adopts as a base material a high temperature wear-resistant aluminum-bronze-based material according to the present embodiment and which is the type having a solid lubricant. Description of Embodiments
  • Hereinafter, a high temperature wear-resistant aluminum-bronze-based material according to an embodiment of the present invention will be described in detail.
  • The high temperature wear-resistant aluminum-bronze-based material according to the present embodiment is a material which contains Al, Ni, Mn, Si, Fe, and Co in respective predetermined amounts in terms of % by mass, with the remainder being Cu.
  • The high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Al content of 9.0% by mass or more and 11.0% by mass or less, and preferably 9.0% by mass or more and 10.0% by mass or less. When the Al content is within the above-described value range, the matrix material can have an appropriate hardness of HV280 or more, thereby improving surface pressure resistance. It is noted that the hardness of the matrix material is measured by a method in accordance with JIS Z2243 2008.
  • When the Al content is less than the above-described value range, hardness becomes insufficient. On the other hand, when the Al content exceeds the above-described value range, hardness becomes high, but toughness becomes low. Therefore, heat resistance is reduced.
  • Also, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Ni content of 1.0% by mass or more and 3.0% by mass or less, and preferably 1.5% by mass or more and 2.5% by mass or less. The inclusion of Ni enables the solubility limit of Al in an α phase to be widened, and also the melting point of the matrix material to be increased thereby improving heat resistance. Furthermore, the inclusion of Ni contributes to deposition of a hard material, together with Fe-Si-Mn described later.
  • When the Ni content is less than the above-described value range, the heat resistance of the matrix material is not satisfied. On the other hand, when the Ni content exceeds the above-described value range, there is the drawback that the matrix material is embrittled, and a manufactured product becomes expensive because Ni is a rare metal.
  • Also, when the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has a structure in which an Fe-Mn-Si-based hard material is dispersed, the wear resistance as a sliding member improves.
  • The high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Mn content of 8.5% by mass or more and 15.0% by mass or less, preferably 8.5% by mass or more and 13.0% by mass or less, and more preferably 8.5% by mass or more and 10.0% by mass or less. When the Mn content is within the above-described value range, Mn, together with Si, Mn and the like described later, causes an Fe-Si-Mn-based hard material to be deposited in the matrix material, thereby improving wear resistance. Also, when the Mn content ratio is increased, the matrix material can have suitable toughness.
  • When the Mn content is less than the above-described value range, toughness which is necessary and sufficient as the matrix material cannot be obtained. When the Mn content exceeds the above-described value range, toughness becomes more than necessary.
  • Also, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Fe content of 0.5% by mass or more and 5.0% by mass or less, preferably 1.0% by mass or more and 5.0% by mass or less, and more preferably 1.5% by mass or more and 5.0% by mass or less. When the Fe content is within the above-described value range, Fe is deposited together with Mn-Si and the like as a hard material in the matrix material, and particularly contributes to a finer structure of the above-described hard material, thereby improving the properties as a sliding member.
  • When the Fe content exceeds the above-described value range, corrosion resistance is reduced. Furthermore, Fe is dissolved to the degree that is the solubility limit (peritecteutectic point) or more thereby to be segregated in the structure, which leads to the increase of a friction coefficient. Therefore, aggression toward a mating material is increased. In consideration of the fact in which a mating material of sliding movements is mainly a steel material, excessive inclusion of Fe is likely to cause adhesion, which leads to reduced sliding properties.
  • Also, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has an Si content of 2.0% by mass or more and 4.0% by mass or less, preferably 2.0% by mass or more and 3.0% by mass or less, and more preferably 2.5% by mass or more and 3.0% by mass or less. When the Si content is within the above-described value range, Si, together with Mn and Fe, causes a eutectic hard material to be deposited, thereby improving sliding properties.
  • Also, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment has a Co content of 0.01% by mass or more and 1.5% by mass or less. According to the present embodiment, the inclusion of Co improves heat resistance.
  • FIGs. 1 to 4 are each a diagram illustrating a configuration of a sliding member which adopts as a base material the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment. FIG. 1 illustrates a plate-like sliding member 1 which is the type having no solid lubricant. FIG. 2 illustrates a plate-like sliding member 2 which is the type having a plurality of pieces of a solid lubricant 3 embedded therein. FIG. 3 illustrates a hollow cylindrical sliding member 4 which is the type having no solid lubricant. FIG. 4 illustrates a hollow cylindrical sliding member 5 which is the type having a plurality of pieces of a solid lubricant 6 embedded therein. It is noted that FIGs. 1 to 4 illustrate examples of the form of a sliding member, and the form of the sliding member is not limited to these embodiments .
  • As illustrated in the drawings, a plurality of pieces of a solid lubricant having a self-lubricating action may be embedded in portions of a sliding surface formed from the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment. Examples of the solid lubricant according to the present embodiment to be used may include solid lubricants, such as a graphite-based solid lubricant, a PTFE-based solid lubricant, a MoS2-based solid lubricant, and a Pb alloy-based solid lubricant.
  • According to the present embodiment, the provision of the sliding surface in which a solid lubricant is embedded causes the lubricant to be dispersed on the sliding surface even in high-temperature environments. Therefore, the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment can have improved sliding properties, and becomes suitable as a sliding member.
  • Also, it is preferable that the high temperature wear-resistant aluminum-bronze-based material according to the present embodiment have a Vickers hardness of HV280 or more, an elongation of 0.5% or more, and a tensile strength of 500 N/mm2 or more. When the hardness is equal to or more than HV280, surface pressure resistance and wear resistance in high-temperature environments are improved.
  • Also, when the elongation is equal to or more than 0.5%, there can be obtained the material strength which is suitable for a sliding member. It is noted that as described herein, the "elongation" refers to an elongation that is measured with a tensile test piece in accordance with JIS Z2241. Also, when the tensile strength is equal to or more than 500 N/mm2 or more, load bearing properties in high-temperature environments are improved. The sliding properties of the present invention will be described in detail by way of examples.
    • Examples
  • Hereinafter, examples of the present invention will be described. It is noted that the present invention is not limited to the following examples.
  • A plurality of copper alloys of the composition as illustrated in Table 1 were melted in a high-frequency furnace and cast with a mold, thereby to prepare a block test piece according to each of Examples 1 to 8 and Comparative Examples 1 to 5. Table 1 indicates composition values [Wt%] of the test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5. The composition values were obtained by ICP emission spectrochemical analysis.
  • As illustrated in Table 1, the test pieces according to Example 1 to Example 8 have a composition in which an Al content was 9.0% by mass or more and 11.0% by mass or less, an Mn content was 8.5% by mass or more and 15.0% by mass or less, an Fe content was 0.5% by mass or more and 5.0% by mass or less, an Ni content was 1.0% by mass or more and 3.0% by mass or less, an Si content was 2.0% by mass or more and 4.0% by mass or less, and a Co content was 0.01% by mass or more and 1.5% by mass or less, with the remainder being substantially Cu.
  • On the other hand, the composition of part of the metals contained in each of Comparative Example 1 to Comparative Example 5 is outside the range of the above-described examples. [Table 1] (all examples except example 3 outside claimed range)
    Cu Al Ni Mn Si Fe Co
    Example 1 Remainder 9.37 1.87 14.80 2.86 4.90 1.00
    Example 2 Remainder 9.22 2.01 8.73 2.95 1.68 1.06
    Example 3 Remainder 9.38 1.73 9.06 3.32 1.16 0.27
    Example 4 Remainder 9.33 1.97 14.30 2.86 1.67 1.02
    Example 5 Remainder 9.23 1.98 8.55 2.35 1.59 0.27
    Example 6 Remainder 9.66 1. 97 10.90 2.87 1.62 1.00
    Example 7 Remainder 9.24 1.91 8.84 2.87 4.75 1.06
    Example 8 Remainder 9.34 2.03 10.80 2.95 4.99 0.047
    Comparative Example 1 Remainder 4.74 2.05 4.17 2.69 5.10 1.05
    Comparative Example 2 Remainder 8.63 0.87 10.26 1.09 2.89 0.28
    Comparative Example 3 Remainder 9.20 0.78 10.35 3.26 0.86 0.27
    Comparative Example 4 Remainder 9.44 0.82 4.80 3.15 1.01 0.28
    Comparative Example 5 Remainder 9.46 0.97 4.54 3.17 1.95 0.37
  • Table 2 indicates measurement results of the hardness and wear amount for the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5. [Table 2] (all examples except example 3 outside claimed range)
    Hardness [HV] Wear amount [µm]
    Example 1 372 42.8
    Example 2 341 42.5
    Example 3 334 42.3
    Example 4 362 40.8
    Example 5 302 40.5
    Example 6 306 36.5
    Example 7 342 35.5
    Example 8 289 35.5
    Comparative Example 1 181 48.0
    Comparative Example 2 321 53.8
    Comparative Example 3 334 51.5
    Comparative Example 4 297 58.8
    Comparative Example 5 410 49.8
  • The hardness was obtained by measuring the Vickers hardness of the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5 at room temperature. As understood from Table 2, the hardness of the test pieces according to Examples 1 to 8 is 280 or more.
  • The wear amount was measured by performing a block-on-ring type sliding test for the block test pieces according to Examples 1 to 8 and Comparative Examples 1 to 5. The condition of the sliding test is a surface pressure of 10 MPa, a sliding speed of 10 m/min, an environment temperature of 250°C, and a sliding distance of 500 m. The sliding test was performed with a dedicated test machine. The block test piece was pressed against a ring test piece in a state where the temperature in the test machine was maintained at 250°C thereby to apply a load, and the ring test piece was rotated at a constant speed. It is noted that S45C (quenched and tempered at high frequency) was used as the ring test piece that is a mating material.
  • As understood from Table 2, the wear amount of the block test pieces according to Examples 1 to 8 is 35.5 µm or more and 42.8 µm or less, indicating that the wear amount is small. On the other hand, the wear amount of the block test pieces according to Comparative Examples 1 to 5 is 48.0 µm or more and 58.8 µm or less, indicating that the wear amount is large. Thus, the effects of the examples of the present invention were confirmed.
  • In particular, the wear amount is 40.8 µm or less in Example 4 to Example 8. Therefore, it is understood that these compositions are preferable. Furthermore, the wear amount is 36.5 µm or less in Example 6 to Example 8. Therefore, it is understood that these compositions are more preferable.
  • As described above, according to the high temperature wear-resistant aluminum-bronze-based material of the present invention, there can be provided a sliding member which has both surface pressure resistance and wear resistance even in high-temperature environments. Furthermore, by reducing the wear amount of the sliding member, the replacement frequency of the sliding member can be drastically reduced in industrial machines of which the sliding members are not easy to replace.

Claims (4)

  1. A high temperature wear-resistant aluminum-bronze-based material, wherein
    an Al content is 9.0% by mass or more and 11.0% by mass or less,
    an Ni content is 1.0% by mass or more and 3.0% by mass or less, an Mn content is 8.5% by mass or more and 15.0% by mass or less,
    an Si content is 2.0% by mass or more and 4.0% by mass or less,
    an Fe content is 0.5% by mass or more and 1.5% by mass or less, and
    a Co content is 0.01% by mass or more and 1.5% by mass or less, with the remainder being substantially Cu.
  2. The high temperature wear-resistant aluminum-bronze-based material according to claim 1, wherein the high temperature wear-resistant aluminum-bronze-based material has a structure in which an Fe-Mn-Si-based hard material is dispersed.
  3. The high temperature wear-resistant aluminum-bronze-based material according to claim 1 or 2, wherein the high temperature wear-resistant aluminum-bronze-based material has a Vickers hardness of HV280 or more, an elongation of 0.5% or more, and a tensile strength of 500 N/mm2 or more.
  4. A sliding member having a base material of the high temperature wear-resistant aluminum-bronze-based material according to any one of claims 1 to 3.
EP16755004.5A 2015-02-24 2016-02-24 High temperature wear-resistant aluminum-bronze-based material Active EP3263721B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015034357 2015-02-24
PCT/JP2016/000987 WO2016136254A1 (en) 2015-02-24 2016-02-24 High temperature wear-resistant aluminum-bronze-based material

Publications (3)

Publication Number Publication Date
EP3263721A1 EP3263721A1 (en) 2018-01-03
EP3263721A4 EP3263721A4 (en) 2018-08-08
EP3263721B1 true EP3263721B1 (en) 2019-05-29

Family

ID=56788159

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16755004.5A Active EP3263721B1 (en) 2015-02-24 2016-02-24 High temperature wear-resistant aluminum-bronze-based material

Country Status (4)

Country Link
US (1) US20180037978A1 (en)
EP (1) EP3263721B1 (en)
JP (1) JP6764397B2 (en)
WO (1) WO2016136254A1 (en)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7213525B2 (en) * 2017-11-13 2023-01-27 トクデン株式会社 Induction heating roller device
CN109788593A (en) 2017-11-13 2019-05-21 特电株式会社 Incude heat generation roller device
CN110106393B (en) * 2019-05-14 2021-04-16 中国兵器科学研究院宁波分院 High-manganese wear-resistant aluminum bronze alloy and preparation method thereof

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62235446A (en) * 1986-04-04 1987-10-15 Kobe Steel Ltd High manganese-aluminum bronze having high strength and superior seizing resistance
JP2866384B2 (en) * 1988-11-04 1999-03-08 オイレス工業株式会社 Aluminum bronze casting with wear resistance for sliding members
JP3300684B2 (en) * 1999-07-08 2002-07-08 清仁 石田 Copper-based alloy having shape memory characteristics and superelasticity, member made of the same, and method of manufacturing the same
JP3929288B2 (en) * 2001-11-09 2007-06-13 大豊工業株式会社 Copper bearing material excellent in high temperature wear resistance and method for producing the same
FR2922898B1 (en) * 2007-10-31 2009-12-04 Auxitrol Sa IMPROVEMENTS IN CU-AL-NI-FE ALLOYS AND PROBE FOR MEASURING A PHYSICAL PARAMETER COMPRISING AN ELEMENT IN SUCH ALLOY
JP5342882B2 (en) * 2009-01-06 2013-11-13 オイレス工業株式会社 High strength brass alloy for sliding member and sliding member
CN102859015B (en) * 2010-05-21 2015-03-04 奥依列斯工业株式会社 High-strength brass alloy for sliding member, and sliding member
EP2578707A4 (en) * 2010-05-31 2013-12-25 Japan Copper Dev Ass Copper-based alloy and structural material comprising same

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
US20180037978A1 (en) 2018-02-08
WO2016136254A1 (en) 2016-09-01
EP3263721A4 (en) 2018-08-08
JP6764397B2 (en) 2020-09-30
JPWO2016136254A1 (en) 2017-12-07
EP3263721A1 (en) 2018-01-03

Similar Documents

Publication Publication Date Title
JP6854797B2 (en) High-strength brass alloys and alloy products
KR102309320B1 (en) Copper alloy, use of a copper alloy, bearing having a copper alloy, and method for producing a bearing composed of a copper alloy
KR101319723B1 (en) Slide bearing composite material, use and method of production
KR101784748B1 (en) Aluminum bronze alloy, method for the production thereof and product made from aluminum bronze
EP2386664A1 (en) High-strength brass alloy for sliding members, and sliding members
KR20120112178A (en) Thrust bearing for turbocharger of internal-combustion engine
KR20090130128A (en) Pb-free copper alloy sliding material and plain bearings
JP4545162B2 (en) Composite sintered sliding member and manufacturing method thereof
EP3263721B1 (en) High temperature wear-resistant aluminum-bronze-based material
CN111630194B (en) Bronze alloy and sliding member using the same
KR101327059B1 (en) Swash plate and method for manufacturing thereof
US20190062876A1 (en) Copper alloy containing tin, method for producing same, and use of same
JP5029942B2 (en) Hot work tool steel with excellent toughness
CN100482825C (en) Aluminium alloy for sliding bearing
US11028463B2 (en) Copper alloy containing tin, method for producing same, and use of same
EP3521465B1 (en) Slide member and method for manufacturing same
KR20190054825A (en) Abrasion-resistant copper alloy and its manufacturing method thereof
KR101599520B1 (en) A grey cast iron
CN107429327B (en) Copper-zinc alloy and use thereof
EP2677051A1 (en) High-strength copper alloy forging
JP2001064741A (en) Use of copper-tin-iron alloy high in tin concentration
US20210355562A1 (en) High-Tensile Brass Alloy And High-Tensile Brass Alloy Product
US20190390302A1 (en) Wear-resistant copper-zinc alloy and mechanical device using same
KR20130029170A (en) A high strength silicon lubricous metal

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20170925

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20180706

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 9/01 20060101AFI20180702BHEP

Ipc: C22C 9/05 20060101ALI20180702BHEP

Ipc: B22D 27/20 20060101ALI20180702BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20181207

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1138295

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190615

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602016014603

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190529

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190930

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190829

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190829

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190830

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1138295

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602016014603

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

26N No opposition filed

Effective date: 20200303

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20200224

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200224

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190929

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20240219

Year of fee payment: 9