Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C23/00—Alloys based on magnesium
  • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
  • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
  • B21J1/02—Preliminary treatment of metal stock without particular shaping, e.g. salvaging segregated zones, forging or pressing in the rough
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C23/00—Alloys based on magnesium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
  • F04B—POSITIVE-DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS
  • F04B39/00—Component parts, details, or accessories, of pumps or pumping systems specially adapted for elastic fluids, not otherwise provided for in, or of interest apart from, groups F04B25/00 - F04B37/00
  • F04B39/0005—Component parts, details, or accessories, of pumps or pumping systems specially adapted for elastic fluids, not otherwise provided for in, or of interest apart from, groups F04B25/00 - F04B37/00 adaptations of pistons
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
  • F04B—POSITIVE-DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS
  • F04B39/00—Component parts, details, or accessories, of pumps or pumping systems specially adapted for elastic fluids, not otherwise provided for in, or of interest apart from, groups F04B25/00 - F04B37/00
  • F04B39/12—Casings; Cylinders; Cylinder heads; Fluid connections
  • F04B39/121—Casings
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F04—POSITIVE - DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS FOR LIQUIDS OR ELASTIC FLUIDS
  • F04B—POSITIVE-DISPLACEMENT MACHINES FOR LIQUIDS; PUMPS
  • F04B39/00—Component parts, details, or accessories, of pumps or pumping systems specially adapted for elastic fluids, not otherwise provided for in, or of interest apart from, groups F04B25/00 - F04B37/00
  • F04B39/12—Casings; Cylinders; Cylinder heads; Fluid connections
  • F04B39/122—Cylinder block
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
  • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
  • F05C2201/00—Metals
  • F05C2201/02—Light metals
  • F05C2201/028—Magnesium

Definitions

• the present invention relates to a magnesium alloy member containing aluminum, calcium, and manganese; a compressor for air conditioners using the magnesium alloy member as or for a mechanical part of the compressor, and a method for manufacturing the magnesium alloy member.
• Magnesium alloys having a low specific gravity may be used for automotive parts in order to reduce the weight thereof. Magnesium alloys have conventionally been used mainly for parts such as casings and covers which need neither high strength nor heat resistance. However, there have recently been developed magnesium alloys having enhanced strength or heat resistance. For example, Patent Documents 1 to 3 disclose a magnesium alloy having enhanced castability and heat resistance, whereas Patent Document 4 discloses a magnesium alloy having enhanced high-temperature strength and forgeability.
• Compressors for automotive air conditioners are installed in the vicinity of engines so that they are exposed to a temperature of from about 100°C to 150°C.
• Materials for the parts of the compressors therefore have preferably heat resistance.
• mechanical parts engaged in compression work of the compressor have preferably a high fatigue strength at high temperatures.
• Magnesium alloys disclosed in Patent Documents 1 to 3 are however used for casting and have insufficient mechanical strength. They are not suited for use for parts of compressors or the like having preferably high strength at high temperatures.
• Objects of the invention are therefore to provide a magnesium alloy member and a method for manufacturing a magnesium alloy member, each capable of realizing mechanical strength and high-temperature fatigue strength facilitating application thereof to mechanical parts of a compressor for automotive air conditioners; and to provide a compressor for air conditioners equipped with mechanical parts made of a magnesium alloy having necessary mechanical strength and high-temperature fatigue strength.
• the present invention is characterized in a magnesium alloy cast material containing, on the basis of mass%, from 0.3% to 10% calcium, from 0.2% to 15% aluminum, and from 0.05% to 1.5% manganese, and containing calcium and aluminum at a calcium/aluminum mass ratio of from 0.6 to 1.7, with the balance being magnesium and inevitable impurities is subjected to plastic working at from 250°C to 500°C.
• the magnesium alloy member after plastic working at from 250°C to 500°C has, as mechanical strength and high-temperature fatigue strength which mechanical parts of a compressor for automotive air conditioners are desired to have, a 0.2% proof stress at room temperature of 300 MPa or greater and a 150°C fatigue strength of 100 MPa or greater.
• plastic working is conducted at below 250°C, the material is not formed and cracks appear because a sufficient strain amount is not produced.
• the temperature exceeds 500°C on the other hand, high-temperature oxidation or partial melting occurs and an effect for enhancing the fatigue strength may not be expected.
• the plastic working may be followed by solution heat treatment and artificial aging treatment. It is preferred to conduct, after the plastic working, solution heat treatment to retain the resulting magnesium alloy member for 0.08 hour or more at a treatment temperature of from 450°C to 510°C and then conduct artificial aging treatment to retain it for 0.3 hour or more at a treatment temperature of from 150°C to 250°C.
• solution heat treatment is conducted at a treatment temperature ranging from 450°C to 510°C
• the grain boundaries or inside of the grains are reinforced by fine precipitates. This suppresses local deformation and widens a uniform deformation region, so that work softening at high temperatures does not occur easily, leading to enhancement in high-temperature fatigue strength.
• the solution heating conducted at a treatment temperature below 450°C makes it difficult to form a solid solution, reduces an amount of precipitates at the grain boundaries and in the grains, and prevents formation of an appropriate state, so that enhancement in high-temperature fatigue strength is not expected.
• the solution heating is conducted at a treatment temperature exceeding 510°C, on the other hand, burning to melt a portion of the alloy occurs, leading to the formation of pore defects.
• the solution heating time below 0.08 hour may not achieve sufficient solution heat treatment, and thus, retention time preferably exceeds 0.08 hour.
• Cooling employed for hardening may be conducted with warm water or with a certain additive. Various means may be employed insofar as the well-known cooling means for hardening.
• Artificial aging treatment is conducted at a temperature below 150°C, it takes longer to enhance the hardness to a proper one. Treatment temperatures exceeding 250°C may deteriorate the hardness and strength, so that the artificial aging treatment is conducted preferably in a temperature range of from 150 to 250°C.
• the retention time for the artificial aging treatment is below 0.3 hour, sufficient aging hardening is not achieved, and thus, the retention time for the artificial aging treatment is preferably 0.3 hour or more.
• extrusion processing can be conducted. Extrusion processing at from 250°C to 500°C can enhance the fatigue strength while suppressing cracks or surface oxidation.
• the above-mentioned magnesium alloy members can be used as or for mechanical parts of a compressor for air conditioners.
• the present invention makes it possible to provide a magnesium alloy member capable of realizing mechanical strength and high-temperature fatigue strength sufficient to use it as or for mechanical parts of a compressor for automotive air conditioners, more specifically, a 0.2% proof stress at room temperature of 300 MPa or greater and a 150°C fatigue strength of 100 MPa or greater.
• the invention makes it possible to provide a compressor for air conditioners using such a magnesium alloy member as or for the mechanical parts of it.
• a magnesium alloy member having substantially equal mechanical strength and high-temperature fatigue strength to those of high-strength aluminum alloy can be realized, so that the high-strength aluminum alloy can be replaced by the magnesium alloy member having a lower specific gravity than the high-strength aluminum alloy, making it possible to realize a drastic weight reduction of a compressor for automotive air conditioners.
• Table 1 includes tensile strength (MPa) at room temperature, for example, from 10°C to 35°C and a 0.2% proof stress (MPa) of each of a plurality of magnesium alloy samples varied in aluminum (Al), calcium (Ca), and manganese (Mn) contents (mass%).
• MPa tensile strength
• MPa 0.2% proof stress
• Al aluminum
• Ca calcium
• Mn manganese contents
• the "300 MPa”, that is, a desired value of a 0.2% proof stress is set using, as a reference value, the 0.2% proof stress of an aluminum alloy forged material subjected to T6 treatment, that is, solution heat treatment followed by artificial aging treatment.
• This aluminum alloy forged material is used for mechanical parts of a compressor for automotive air conditioners.
• Table 1 The samples listed in Table 1 were each obtained by preparing a magnesium alloy cast material having a content as described in this table and then subjecting it to plastic working, more specifically, hot indirect extrusion processing. These samples had not been subjected to heat treatment (T6 treatment).
• alloy melting was conducted in the atmosphere by using an electric resistance furnace and a mixed gas of SF 6 and CO 2 was used for preventing oxidation of the molten metal. After stirring, bubbling was conducted by supplying an Ar gas in order to remove an oxide formed at the time of Ca addition. The resulting mixture was then cast in a billet mold and thus, the cast material was prepared.
• a hydraulic press was used for direct extrusion processing. The material sample to be extruded was charged in a mold heated to 350°C. After retention for 10 minutes, extrusion processing was started while setting an extrusion ratio at 20. It is to be noted that the term "extrusion ratio" means a (cross-sectional area before plastic working)/(cross-sectional area after plastic working) ratio.
• Example 1 the samples of Examples 1 to 11 were obtained by subjecting a cast material of a magnesium alloy containing from 0.3% to 10% calcium (Ca), from 0.2% to 15% aluminum (Al), and from 0.05% to 1.5% manganese (Mn), having a calcium (Ca)/aluminum (Al) mass ratio of from 0.6 to 1.7, with the balance being magnesium Mg and inevitable impurities to plastic working (extrusion processing) at 350°C.
• a cast material of a magnesium alloy containing from 0.3% to 10% calcium (Ca), from 0.2% to 15% aluminum (Al), and from 0.05% to 1.5% manganese (Mn), having a calcium (Ca)/aluminum (Al) mass ratio of from 0.6 to 1.7, with the balance being magnesium Mg and inevitable impurities to plastic working (extrusion processing) at 350°C.
• samples of Comparative Examples 1 to 7 were obtained by subjecting a cast material of a magnesium alloy which did not satisfy at least one of the above-mentioned ranges of the calcium (Ca) content, the aluminum (Al) content, the manganese (Mn) content, and the calcium (Ca)/aluminum (Al) mass ratio to plastic working (extrusion processing) at 350°C.
• Ca+Al in Table 1 means a total mass% of calcium (Ca) and aluminum (Al).
• the samples of Comparative Examples 1 and 4 having a calcium (Ca) content outside the range of from 0.3% to 10% and the samples of Comparative Examples 2 and 3 having an aluminum (Al) content outside the range of from 0.2% to 15% have a 0.2% proof stress below 300 MPa, that is, the desired value. Thus, it is impossible that they are not suited for use as a mechanical part of a compressor.
• a magnesium alloy preferably satisfies the following conditions, that is, a calcium (Ca) content of from 0.3% to 10%, an aluminum (Al) content of from 0.2% to 15%, a manganese (Mn) content of from 0.05% to 1.5%, and a calcium (Ca)/aluminum (Al) mass ratio of from 0.6 to 1.7 in order to achieve the mechanical strength necessary for mechanical parts of a compressor for automotive air conditioners, more specifically, to achieve a 0.2% proof stress of 300 MPa or greater.
• a Mg-Ca-based compound and a Mg-Al-Ca-based compound are crystallized at the grain boundaries, leading to enhancement in mechanical strength at room temperature and heat resistance.
• the calcium (Ca)/aluminum (Al) mass ratio is adjusted to from 0.6 to 1.7 as in Examples 1 to 11, Mg 2 Ca which is a Mg-Ca-based compound and (Mg,Al) 2 Ca which is an Mg-Al-Ca-based compound are crystallized simultaneously, which is presumed to lead to enhancement in mechanical strength and heat resistance.
• Example 1 Ca [wt%] Al [wt%] Mn [wt%] Ca/Al [-] Ca+Al [wt%] Tensile strength [MPa] 0.2% proof stress [MPa] Rating Example 1 0.34 0.54 0.29 0.63 0.88 328 312 ⁇ Example 2 1.5 2.4 0.23 0.63 3.9 350 335 ⁇ Example 3 3.3 3.7 0.33 0.89 7 349 330 ⁇ Example 4 3 5 0.31 0.60 8 340 330 ⁇ Example 5 5.8 8.1 0.36 0.72 13.9 339 321 ⁇ Example 6 7.6 6.8 0.39 1.12 14.4 327 319 ⁇ Example 7 9.4 8.2 0.43 1.15 17.6 321 310 ⁇ Example 8 9.2 5.8 0.24 1.59 15 322 309 ⁇ Example 9 3.8 14.5 0.37 0.26 18.3 318 304 ⁇ Example 10 3.7 3.9 0.06 0.95 7.6 329 318 ⁇ Example 11 0.33 0.23 0.26 1.43 0.56 321 304 ⁇ Comp.
• the samples listed in Table 2 are the cast materials of a magnesium alloy of Example 3 having the contents indicated in Table 1, that is, a calcium (Ca) content of 3.3%, an aluminum (Al) content of 3.7%, and a manganese (Mn) content of 0.33%, a calcium (Ca)/aluminum (Al) mass ratio of 0.89, and a total content of calcium (Ca) and aluminum (Al) of 7%.
• These cast materials were subjected to extrusion processing (plastic working) at varied extrusion ratios and extrusion temperatures and the results of a 0.2% proof stress test of the samples obtained by extrusion processing are listed.
• the extrusion ratio was set at four ratios, that is, 10, 20, 40, and 60. When the extrusion temperature at each of these extrusion ratios was in a range of from 250°C to 500°C, neither cracks nor surface oxidation occurred and the 0.2% proof stress exceeded the desired value, that is, 300 MPa.
• Table 3 includes measurement results of a 150°C fatigue strength (high-temperature fatigue strength) of a sample subjected to plastic working (extrusion processing) at from 250°C to 500°C, followed by heat treatment (T6 treatment) and a sample not subjected to heat treatment (T6 treatment) after the plastic working.
• the 150°C fatigue strength of an Al alloy forged material (A4032-T6) which is a material specified by JIS is also listed for comparison in Table 3.
• this Al alloy forged material (A4032-T6) has been used for a compressor for automotive air conditioners, and thus, a material capable of achieving a 150°C fatigue strength at least equal to the 150°C fatigue strength of this A4032-T6 (100 MPa) can be used as a substitute member of A4032-T6.
• the fatigue test (rotary bending test) for finding the fatigue strength of Table 3 and calculation of a fatigue strength were conducted in accordance with " The Japan Society of Mechanical Engineers, Standard method of statistical fatigue testing (revised) JSME S-002-1994" ed.
• the test was conducted at a test temperature of 150°C, a rotating speed of 3000rpm, a frequency of 50Hz, and a stress ratio R of -1.
• the fatigue strength in Table 3 is the result of the tests conducted 10 7 times.
• the test specimen used for the fatigue test is a rod-type test specimen.
• the diameter at a chuck portion was 8.5 mm and the diameter at a breaking portion was 4 mm. It was collected so that the extruding direction and the load applying direction were orthogonal to each other.
• the breaking portion was polished with waterproof abrasive paper, followed by buffing to finish.
• solution heat treatment to retain the sample in an Ar gas stream of 500°C for 30 minutes (0.5 hour) was conducted in a horizontal tubular furnace and then, artificial aging treatment was conducted in an oil bath of 180°C for 2 hours.
• the heat treatment time retention time is a period of time starting with the charging of the sample.
• the 150°C fatigue strength of A4032-T6 is 100 MPa; the 150°C fatigue strength of the magnesium alloy member subjected to plastic working at a temperature of from 250°C to 500°C, more specifically, subjected to extrusion processing at 350°C and not subjected to the heat treatment (T6 treatment) thereafter was 117 MPa; and the 150°C fatigue strength of the magnesium alloy member having the same composition, subjected to the same plastic working, and then subjected to the heat treatment (T6 treatment) was 132 MPa.
• the 150°C fatigue strength exceeding that of A4032-T6 can be achieved by subjecting the magnesium alloy cast material having a calcium (Ca) content of from 0.3% to 10%, an aluminum (Al) content of from 0.2% to 15%, a manganese (Mn) content of from 0.05% to 1.5%, and a calcium (Ca)/aluminum (Al) mass ratio of from 0.6 to 1.7 to plastic working at from 250 to 500°C even without subjecting it to heat treatment (T6 treatment).
• the material subjected to the heat treatment (T6 treatment) in addition to the plastic working has an enhanced 150°C fatigue strength compared with the material not subjected to the heat treatment (T6 treatment).
• a magnesium alloy member obtained by subjecting the magnesium alloy cast material having a calcium (Ca) content of from 0.3% to 10%, an aluminum (Al) content of from 0.2% to 15%, a manganese (Mn) content of from 0.05% to 1.5%, and a calcium (Ca)/aluminum (Al) mass ratio of from 0.6% to 1.7 to plastic working at from 250°C to 500°C can achieve a room-temperature 0.2% proof stress and a high-temperature fatigue strength suited for use for mechanical parts of a compressor for automotive air conditioners, more specifically, the room-temperature 0.2% proof stress of 300 MPa or greater and 150°C fatigue strength of 100 MPa even without the heat treatment (T6 treatment).
• the member subjected to the heat treatment (T6 treatment) in addition to the plastic working has a further enhanced high-temperature fatigue strength. It is therefore possible to use a magnesium alloy member instead of a conventionally used high-strength aluminum alloy for the formation of mechanical parts of a compressor for automotive air conditioners. This makes it possible to realize a remarkable reduction in the weight of the compressor.
• the solution heat treatment after plastic working (extrusion processing) be conducted while retaining the magnesium alloy member for 0.08 hour or more at a treatment temperature of from 450°C to 510°C and the artificial aging treatment after hardening treatment is conducted while retaining the member for 0.3 hour or more at a treatment temperature of from 150°C to 250°C.
• the solution heat treatment after plastic working (extrusion processing) be conducted while retaining the magnesium alloy member for 0.08 hour or more at a treatment temperature of from 450°C to 510°C and the artificial aging treatment after hardening treatment is conducted while retaining the member for 0.3 hour or more at a treatment temperature of from 150°C to 250°C.
• the grain boundaries and the inside of the grains are reinforced with fine precipitates, local deformation is suppressed, and a uniform deformation area is widened, so that work softening at high temperatures is suppressed and the resulting alloy member has an enhanced high-temperature fatigue strength.
• the solution heating conducted at a treatment temperature below 450°C makes it difficult to form a solid solution, reduces an amount of precipitates at the grain boundaries and in the grains, and prevents formation of an appropriate state, so that enhancement in high-temperature fatigue strength is not expected.
• the solution heating is conducted at a treatment temperature exceeding 510°C, on the other hand, burning to melt a portion of the alloy occurs, leading to the formation of pore defects.
• the solution heating time below 0.08 hour may not achieve sufficient solution heat treatment, and thus, retention time is preferably greater than 0.08 hour.
• Treatment temperatures of the artificial aging treatment below 150°C may increase the treatment time in order to attain a proper hardness, whereas treatment temperatures exceeding 250°C deteriorate the hardness and strength.
• the temperature of the artificial aging treatment is preferably in a range of from 150°C to 250°C. Retention time of the artificial aging treatment below 0.3 hour cannot achieve sufficient aging hardening, and thus, the retention time of the artificial aging treatment is preferably 0.3 hour or greater.
• the temperature and retention time of the heat treatment (T6 treatment) which have provided the results of Table 3 satisfy the above-mentioned temperature range and time range.
• the magnesium alloy member and the method for manufacturing the magnesium alloy member according to the invention can realize a room-temperature 0.2% proof stress of 300 MPa or greater and a 150°C fatigue strength of 100 MPa or greater which are necessary for mechanical parts of a compressor for automotive air conditioners and therefore the magnesium alloy member of the invention can be used instead of the conventionally used Al alloy forged material A4032. Since the magnesium alloy member has a lower specific gravity than the Al alloy forged material A4032, when mechanical parts of a compressor for automotive air conditioners are made of the magnesium alloy, it is possible to markedly reduce the weight of the compressor, reduce the weight of the automotive, and therefore enhance the fuel efficiency.
• Examples of the magnesium alloy member of the invention and mechanical parts of a compressor for automotive air conditioners to which the magnesium alloy member is applied include shoes and pistons for swash plate compressors and spiral bodies for scroll type compressors.
• the magnesium alloy member and the method for manufacturing a magnesium alloy member according to the invention have been developed with a view to applying them to mechanical parts of a compressor for automotive air conditioners, but they can be applied not only to the mechanical parts of a compressor for automotive air conditioners but also to mechanical parts of a compressor for stationary air conditioners.
• the plastic working is not limited to extrusion processing and it may be forging, rolling, or drawing processing.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
• Organic Chemistry (AREA)
• Metallurgy (AREA)
• Materials Engineering (AREA)
• Crystallography & Structural Chemistry (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• General Engineering & Computer Science (AREA)
• Compressor (AREA)
• Extrusion Of Metal (AREA)
• Forging (AREA)

Applications Claiming Priority (2)

Publications (2)

Family

ID=45994031

Family Applications (1)

Country Status (6)

Cited By (3)

Families Citing this family (13)

Citations (6)

Family Cites Families (6)

• 2010
  • 2010-10-29 JP JP2010244816A patent/JP2012097309A/ja active Pending
• 2011
  • 2011-10-28 KR KR1020137013196A patent/KR20130101100A/ko not_active Application Discontinuation
  • 2011-10-28 WO PCT/JP2011/074959 patent/WO2012057329A1/fr active Application Filing
  • 2011-10-28 US US13/882,470 patent/US20130213528A1/en not_active Abandoned
  • 2011-10-28 CN CN2011800520477A patent/CN103180472A/zh active Pending
  • 2011-10-28 EP EP11836462.9A patent/EP2631312A4/fr not_active Withdrawn

Patent Citations (6)

Non-Patent Citations (2)

Also Published As

Similar Documents

Legal Events