• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    The invention provides a hard particle powder for sintered body, which contains in mass%, 2% to 3.5% Si, 6% to 10% Cr, 20% to 35% Mo, 0.01%. at 0.5% REM, the rest being Co and unavoidable impurities. The invention further provides a sintered body obtained by a step of mixing the above-mentioned sintered hard particle powder with a pure iron powder and a graphite powder to obtain a powdery mixture, a step of shaping for compacting and shaping the powdery mixture so as to obtain a compact, and a sintering step of the compact. The hard particle powder according to the invention has the effect of producing a sintered body having improved wear resistance, without substantially altering the powder characteristics and the sintering characteristics. In addition, the sintered body according to the invention has the effect of having excellent wear resistance.
    公开号:BE1018371A3
    申请号:E2008/0697
    申请日:2008-12-23
    公开日:2010-09-07
    发明作者:Yamamoto Tomomi；Kurata Seiji
    申请人:Daido Steel Co Ltd；
    IPC主号:
    专利说明:

    Hard particle powder for sintered body and sintered body.
    FIELD OF 1 / INVENTION
    The present invention relates to a hard particle powder for sintered body and a sintered body. More particularly, the invention relates to a technique for improving the wear resistance of automotive engine valve seats by adding REM to a hard particle powder, without substantially altering powder characteristics and sintering characteristics.
    BACKGROUND OF THE INVENTION
    Tribaloy T-400 is known as hard particles having high wear resistance, which are based on hard phase cobalt, consisting essentially of molybdenum silicide. A Co-2.5Si-28Mo-8.5Cr alloy powder, which is a comparable material to the Tribaloy T-400, has been used in large quantities as hard particles contributing greatly to the wear resistance of valve seats automotive engines (hereinafter referred to simply as "valve seats") in automotive engines operating under heavy load. Therefore, a series of techniques has been proposed.
    For example, patent document 1 describes, for the purpose of dispersing a greater amount of hard coat in a matrix without altering wear resistance, strength, etc., a method of producing a sintered element. wear resistant, which comprises compacting and forming a raw powder containing a matrix powder (iron, SUS316, SUS304, SUS310 or SUS430) and a powder forming the hard layer (Co-28-Mo-2, 5Si-8Cr), followed by sintering of the compact, where at least 90% by weight of the matrix powder is a fine powder having a maximum particle diameter of 46 μm, and the proportion of powder forming the hard layer in the powder gross is 40-70% by mass.
    Patent Document 2 discloses, for the purpose of obtaining an iron-based sintered alloy material having excellent wear resistance, a method for producing an iron-based alloy material resistant to abrasion. wear for valve seats, where 100 parts by weight of an iron-based alloy powder are composed of a pure iron powder, an iron alloy powder, a carbon powder, a powder of steel having a fine carbide deposit, and a hard particle powder (eg Cr-Mo-Co system or Ni-Cr-Mo-Co system) are mixed with 0.2-3.0 parts by weight of a solid lubricant powder (sulfide or fluoride) and / or 0.2-5.0 parts by weight of a stabilized oxide powder (Y 2 O 3 or CeO 2, each of which is an oxide of a rare earth element, or CaTiOs), and the resultant iron-base alloy powder is compacted and shaped, and then sintered compact to obtain a sintered body.
    Patent Document 1: JP-A-2007-107304
    Patent Document 2: JP-A-2007-193173
    SUMMARY OF THE INVENTION
    However, with the trend toward higher loads resulting from the required engine characteristics, the wear resistance required of valve seat materials is also increasing. There is therefore a problem that the hard particles described, for example in the patent documents 1 and 2, can not satisfactorily achieve the required wear resistance of the valve seat materials. In addition, it is believed that when attempting to achieve the improved wear resistance required for valve seat materials, powder characteristics and sintering characteristics are impaired. There is therefore a desire for a technique that is able to achieve the improved wear resistance required for valve seat materials without altering powder characteristics and sintering characteristics.
    The invention has been made in this spirit. An object of the invention is to provide a sintered body hard particle powder, which can provide a valve seat having improved wear resistance, without substantially altering powder characteristics and sintering characteristics. Another object of the invention is to provide a sintered body having excellent wear resistance.
    In order to overcome the problems described above, the present inventors have diligently carried out studies on the techniques for improving the wear resistance of the valve seats using a Co-2 alloy powder, 5Si-28MB-8,5Cr. During the course of the studies, the inventors have discovered that the wear resistance of the valve seats can be improved by adding REM to the hard particles. It has also been discovered that the addition of REM to hard particles does not alter the characteristics of the powder or the sintering characteristics.
    The invention was carried out on the basis of these findings. Namely, the invention provides a hard particle powder for sintered body, which comprises in% by weight, 2% to 3.5% Si, 6% to 10% Cr, 20% to 35% Mo, 0 , 01% to 0.5% REM, the rest being Co and unavoidable impurities.
    In this case, the hard particle powder for sintered body according to the invention may also contain 0.1% by mass or less of C and 1% by mass or less of Mn.
    The invention further proposes, to overcome the problems, a sintered body obtained by a step of mixing the hard particle powder mentioned above for sintered body according to the invention, with a pure iron powder and a graphite powder. to obtain a powdery mixture, a shaping step for compacting and shaping the powdery mixture so as to obtain a compact, and a sintering step of the compact.
    The hard particle powder according to the invention has the effect of giving a sintered body having improved wear resistance without substantially altering the characteristics of the powder and the sintering characteristics, because it contains in% by mass, 2% at 3.5% Si, 6% to 10% Cr, 20% to 35% Mo, 0.01% to 0.5% REM. Therefore, this powder is particularly suitable for use as a valve seat material.
    The sintered body according to the invention has the effect of having excellent wear resistance because it is a sintered body obtained by using the hard particle powder for sintered body according to the invention as raw material.
    The sintered body hard powder and the sintered body according to the invention are effective in improving the wear resistance of valve seats without altering the characteristics of the powder or the sintering characteristics. Therefore, the hard particle powder and the sintered body according to the invention have a high industrial value in the automotive industry and in different neighboring industries.
    BRIEF DESCRIPTION OF THE DRAWINGS
    Fig. 1 is a sectional view diagrammatically illustrating a wear tester for testing the valve seat itself.
    Fig. 2 is a view illustrating a portion where the wear loss of a wear test piece is measured.
    Fig. 3 is a graph obtained showing the relationship between the wear loss of the wear test pieces and the EMR content.
    BEST MODE FOR CARRYING OUT THE INVENTION
    Embodiments of the invention will be explained below, in detail with reference to the drawings.
    Composition of hard particle powder for sintered body
    The sintered body hard powder of the invention contains silicon (Si), chromium (Cr), molybdenum (Mo) and EMR as essential components in addition to cobalt (Co) as the base. The carbon (C) and manganese (Mn) contents, which are the inevitable impurities in the powder, can be controlled with certainty.
    The reasons for the limitations on the contents of these elements are explained below. Here, in the present description, all percentages defined by mass are the same as those defined by weight, respectively.
    (1) 2% by mass <If <3.5% by mass
    Silicon (Si) is an ingredient incorporated for the purpose of improving hardness by forming a silicide. The reason why the lower limit of the amount of silicon is 2% by weight is that the powder particles having a silicon content lower than the lower limit are of too low hardness to function as hard particles. The reason why the upper limit of the amount of silicon is 3.5% by weight is that the powder particles having a silicon content higher than the upper limit have too much hardness and therefore give a sintered body (seat of valve) which suffers from a loss of powder particles due to cracking and has an increased wear loss.
    (2) 6% by weight <chromium <10% by weight
    Chromium (Cr) is an ingredient incorporated for the purpose of maintaining oxidation resistance. The reason why the lower limit of the amount of chromium is 6% by weight is that the powder particles having a chromium content lower than the lower limit have insufficient oxidation resistance. On the other hand, the reason why the upper limit of the amount of chromium is 10% by weight is that the powder particles having a chromium content higher than the upper limit are impaired in the sintering properties.
    (3) 20% by mass <molybdenum <35% by weight
    Molybdenum (Mo) is an ingredient incorporated for the purpose of maintaining the hardness of the powder particles. The reason why the lower limit of the amount of molybdenum is 20% by weight is that the powder particles having a molybdenum content lower than the lower limit result in a sintered body having insufficient wear resistance. On the other hand, the reason why the upper limit of the amount of molybdenum is 35% by weight is that the powder particles having a molybdenum content higher than the upper limit have a too high hardness and therefore give a sintered body , which suffers from a loss of powder particles due to cracking and has an increased wear loss.
    (4) 0.01% by mass <REM <0.5% by mass
    In the invention, the term REM means at least one type of lanthanoid elements. REM is an ingredient incorporated for the purpose of improving the wear resistance of the sintered body without altering the characteristics of the powder and the sintering characteristics. The reason why the lower limit of the amount of REM is 0.01% by weight is that the incorporation of REM in an amount below the lower limit makes almost no contribution to an improvement in wear resistance. of the sintered body. On the other hand, the reason why the upper limit of the amount of REM is 0.5% by weight is that the incorporation of REM in an amount exceeding the upper limit also does not contribute to an improvement in resistance to wear and causes oxidation of a large quantity of the powder particles, which results in poor sintering characteristics. The content of REM is preferably at 0.2% by mass or less
    The sintered body hard particle powder of the invention may further contain 0.1% by weight or less of carbon (C) and 1% by weight or less of manganese (Mn).
    The reason why the upper limit of the amount of carbon is 0.1% by weight is to inhibit the deterioration of toughness due to carbide formation.
    The reason that the upper limit of the amount of manganese is 1% by weight is that the incorporation of manganese in an amount exceeding the upper limit causes the oxidation of a larger quantity of powder particles, which results in poor sintering characteristics.
    The reasons for the remainder cobalt (Co) and unavoidable impurities is that cobalt is the base of the sintered body hard powder of the invention.
    In summary, the sintered body hard particle powder of the invention is more preferably a sintered body hard particle powder, which contains in mass%, 2% to 3.5% Si, 6% by weight. 10% Cr, 20% to 35% Mo, 0.01% to 0.5% REM, 0.1% or less C, 1% or less of Mn, and the balance being Co and impurities inevitable.
    Process for producing the sintered body
    The sintered body of the invention can be obtained by: a step of mixing the sintered body hard particle powder having the above composition, with a pure iron powder and a graphite powder to obtain a powdery mixture, a step of shaping and compacting the powdery mixture to obtain a compact, and a sintering step of the compact. In the mixing step, it is preferred to add a lubricant for compaction. In addition, it is desirable to perform a degreasing before sintering.
    Examples
    Examples according to the invention and comparative examples are explained below.
    Production of hard particle powders
    For each of Examples 1 to 5 and Comparative Examples 1 to 6, the ingredient elements given in Table 1 are mixed in the proportion given in the table to give the hard particle powder.
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    I-I
    '<ΰ cd υ ρ m
    Ρ C0 Η C0 'φ U
    φ τ3 ρ C0
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    CG
    Ρ C0 Ρ r ~ Η ρ
    CG
    'CD
    Μ
    CG
    (D
    Μ Ρ
    Ti CG CD I-1 Ρ υ Η Ρ Ρ (Ο & 8 ^
    u CG
    CO 2
    CD
    • TS φ Ρ 0 R CG Qj
    CD
    Ti CG
    CG Ρ Ο Ο Η Η Η Η Η Η Η Η Η Η Η Η Η Η Η Η
    Examination of the characteristics of the powder
    Of the hard particle powders produced, the hard particle powders of Example 1 and Comparative Example 1 are examined for powder characteristics (particle size distribution, bulk density, flowability, and hardness of the powder). The particle size distribution is determined according to the Japan Powder Metallurgy Standard Association JPMAP P 02-1992, the apparent specific gravity according to Japan Powder Metallurgy Standard Association JPMAP P 06-1992, and the flowability according to Japan. Powder Metallurgy Association Standard JPMAP P 07-1992. In addition, the hardness of the powder is measured with a hardness tester.
    in
    α) s-ι
    V
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    CU
    m Φ d m ω
    D
    D1
    • H
    4-> in CNJ Ή 3 'Φ (0 4-> ο) υ «-l Γ0
    Λ M
    m fö η u
    Production of sintered bodies
    With respect to each of Examples 1 to 5 and Comparative Examples 1 to 6, sintered bodies are produced by the following procedure under the conditions of production of wear-test pieces shown in Table 1.
    First, 69.9% by weight of pure iron powder (ASC100.29) is mixed with 30% by weight of the hard particle powder and 0.8% by weight of graphite (CPB). To 100 parts by weight of the resulting mixture, 0.5 part by weight of Zn-St (lubricant for compaction) is added. The ingredients are mixed to obtain a crude powder mixture for sintered body.
    Next, the crude powder mixtures of Examples 1 to 5 and Comparative Examples 1 to 6 are each compacted at a pressure of 8 t / cm 2. Thus, (1) disc-shaped compacts having a diameter of 35 mm and a thickness of 14 mm are obtained for Examples 1 to 5 and Comparative Examples 1 to 6, and (2) ring-shaped compacts having an outer diameter of 28 mm, an inner diameter of 20 mm, and a thickness of 4 mm are obtained for Example 1 and Comparative Example 1.
    Then, the ring-shaped and ring-shaped compacts of Examples 1 to 5 and Comparative Examples 1 to 6, are degassed at 400 ° C in air for 1 hour, then sintered for 1 hour under an atmosphere of decomposed ammonia (N2 + 3¾), having a temperature of 1160 ° C, to obtain the sintered bodies.
    Examining the sintering characteristics
    Among the compacts and sintered bodies produced, we examine the compacts and sintered bodies of Example 1 and Comparative Example 1 concerning the sintering characteristics (specific mass of the compact, sintering specific gravity, chemical components, hardness of the sintered body, resistance to radial crushing, high temperature hardness, thermal diffusivity, specific heat capacity, and thermal conductivity).
    The specific mass of the compact (specific mass of the compact before sintering) and the sintering specific gravity (specific gravity of the sintered body after sintering) are determined according to the Japan Powder Metallurgy Standard Association JPMAP P 09-1992. The chemical components are determined by infrared spectroscopy. The radial crush strength is determined by examination of the sintered ring-shaped sinter (outer diameter 28 mm, inside diameter 20 mm, thickness 4 mm) with an Amsler test machine. The high temperature hardness is measured with a high temperature hardness tester. Thermal diffusivity, specific heat capacity and thermal conductivity are determined by the laser flash method.
    The results of the examination of these characteristics are given in Table 3.
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    σι σ ^ φ Φ + J 4-1 4-1 4-1 Η -Η
    Μ H
    m 4-1 Φ Φ Τ3 Ό w Φ co φ 4-1 Φ σ · η σ σ1 σ σ γ Η CO -Η 4-1 '4-1 Μ ΙΟ 00 · Η 00 · Η
    Μ U
    σ 'Φ σ' Φ (0 4-1 ί0 4-> φ υ φ υ Η (Ο ι-l (Ο XJ Μ Λ Μ (Ο Φ (Ο (Ο Ε-η Ο E-ι Φ
    Wear resistance test of sintered bodies
    The wear tester for evaluating the valve seat itself (hereinafter referred to simply as "wear tester"), shown in Figure 1, is used to perform a sintered body wear test. (disc-shaped sintered bodies produced). First, the disk-shaped sintered bodies (diameter 35 mm, thickness 14 mm) of Examples 1 to 5 and Comparative Examples 1 to 6 are processed into a valve seat shape to obtain the test pieces of the invention. wear. Each piece of the wear test is placed on the wear tester by press fit of the test piece into the seat support. The wear tester is operated under the test conditions given in Table 4. While the wear test piece is kept indirectly heated by heating the valve with a gas flame, the wear test piece is worn by applying a starting threshing force.
    Table 4
    Conditions for the wear resistance test
    Front of the Fe-21Cr-9Mn-4Ni + Co Alloy Valve Valve
    The wear loss of each wear test piece is obtained by measuring the shape of the wear test piece with a shape measuring device before and after the wear resistance test and determining the wear pattern. D difference in the direction perpendicular to the surface of the wear test piece, as shown in Figure 2 (enlarged view of the portion indicated by the arrow A in Figure 1). The results obtained are given in FIG. 3 using a graph obtained by relating the wear-loss relationship of the wear-test pieces to the content of REM (the number assigned to each point on the graph indicates loss of wear (pm)).
    Discussion: Resistance to wear
    Wear resistance is discussed first. As shown in Table 1 and Figure 3, the wear loss of Examples 1 to 5 is less than 20 μm, while the wear loss of Comparative Examples 1 to 6 is 20 μm or more. Thus, Examples 1 to 5 have less wear loss than Comparative Examples 1 to 6.
    Examples 1 to 5 are first compared with Comparative Example 1. The sintered bodies each satisfy the preferred ranges of contents of the components according to the invention, except that the REM is present or not. Therefore, it is found that in the compositions (excluding EMR) of Examples 1 to 5, the addition of REM has the effect of improving the wear resistance of the sintered bodies (valve seats).
    Next, the REM content in the case of the addition of REM in the compositions (without REM) according to Examples 1 to 5 is discussed. It can be seen that when the content of REM is too high as in Comparative Examples 3 and 6, the effect of improving the wear resistance of the sintered bodies (valve seats) is not obtained. These results show that it is desirable that the content of REM does not exceed 0.6% by weight. It is thus found that the content of REM is preferably 0.5% by weight or less, more preferably 0.2% by mass or less.
    The reason why Comparative Example 2 shows increased wear loss may be that too much silicon results in too much hardness and thus loss of powder particles.
    The reason why Comparative Example 3 shows increased wear loss is assumed to be the following. The large amount of REM results in increased powder oxidation, i.e., low sintering characteristics, and the small amount of silicon results in low hardness. In addition, the small amount of chromium results in insufficient resistance to oxidation of the powder particles.
    The reason why Comparative Example 4 shows an increased wear loss may be that too much molybdenum results in too much hardness and thus loss of powder particles.
    The reason why Comparative Example 5 shows increased wear loss is assumed to be the following. The large amount of manganese results in increased powder oxidation, ie altered sintering characteristics, and the large amount of chromium also negatively affects the sintering characteristics.
    Discussion: characteristics other than wear resistance
    Features other than wear resistance (particle size distribution, powder characteristics, and sintering characteristics) are discussed. Table 2 gives the particle size and powder characteristics of Example 1 and Comparative Example 1. By a comparison of these, the particle size distribution and the powder characteristics of Example 1 are judged comparable to the particle size distribution and powder characteristics of Comparative Example 1. In this regard, although the particle size distributions differ in the range -100 to + 145 and range. -145 to +200, these differences are due to a difference in the production of the powder. These differences do not alter the characteristics of Example 1. With regard to the hardness of the powder, Example 1 has a lower value. This is attributable to a difference in the silicon content between the powders, and does not alter the characteristics of Example 1.
    Table 3 shows the sintering characteristics of Example 1 and those of Comparative Example 1. By a comparison between them, the sintering characteristics of Example 1 are judged comparable to the sintering characteristics of Example 1. Comparative Example 1, except that Comparative Example 1 was superior in radial crush strength. It should be noted, however, that the required level of radial crush strength is about 40 kgf / mm 2 and that the radial crush strengths of Example 1 and Comparative Example 1 are much greater than this value. Even if Example 1 is lower than Comparative Example 1, this does not influence the properties of Example 1.
    From these results it is found that the wear resistance of the sintered bodies (valve seats) can be improved without substantially altering the powder characteristics and the sintering characteristics by adding REM to a hard particle powder composed of indicated compounds. It is also found that sintered bodies having excellent wear resistance can thus be obtained.
    Although the invention has been described with reference to its embodiments, it should not be construed as being limited to the embodiments in any way. Although the invention is particularly suitable for use as a valve seat, the applications of the invention should not be construed as limited to valve seats and the invention can be applied to valve guides and other mechanical parts. structural.
    This application is based on the Japanese patent application. No. 2007-333736 filed December 26, 2007, the content of which is incorporated herein by reference.
    LEGEND OF FIGURES
    1 valve 2 gas burner 3 flame 4 wear test piece (valve seat) 5, seat support 6 cooling water 7 valve guide 8 spring 9 retention cap 10 wash bar
    权利要求:
    Claims (2)
    [1]
    1. Hard particle powder for sintered body, which comprises in% by weight, 2% to 3.5% Si, 6% to 10% Cr, 20% to 35% Mo, 0.01% to 0, 5% REM, the rest being Co and the inevitable impurities.
    [2]
    2. Sintered body obtained by a step of mixing the hard particle powder for sintered body according to claim 1, a pure iron powder and a graphite powder to obtain a powdery mixture, a shaping step for compaction and shaping the powdery mixture so as to obtain a compact, and a sintering step of the compact.
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    同族专利:
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    引用文献:
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    JP2007333736A|JP5125488B2|2007-12-26|2007-12-26|Hard particle powder for sintered body and sintered body|
    JP2007333736|2007-12-26|
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