CA2018636C - Precipitation hardening ferritic-pearlitic steel - Google Patents
Precipitation hardening ferritic-pearlitic steel Download PDFInfo
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- CA2018636C CA2018636C CA002018636A CA2018636A CA2018636C CA 2018636 C CA2018636 C CA 2018636C CA 002018636 A CA002018636 A CA 002018636A CA 2018636 A CA2018636 A CA 2018636A CA 2018636 C CA2018636 C CA 2018636C
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
- F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Catalysts (AREA)
- Output Control And Ontrol Of Special Type Engine (AREA)
Abstract
The present invention relates to a precipitation hardening ferritic-pearlitic steel which is especially adapted for use with reciprocating valves in internal combustion engines. The steel according to the invention typically contains from 0.20 to 0.60%
carbon, 0.20 to 0.95% silicon, 0.50 to 1.80% manganese, 0.004 to 0.04% nitrogen and 0.05 to 0.20% vanadium and/or niobium. The balance of the steel is comprised of iron and incidental impurities.
carbon, 0.20 to 0.95% silicon, 0.50 to 1.80% manganese, 0.004 to 0.04% nitrogen and 0.05 to 0.20% vanadium and/or niobium. The balance of the steel is comprised of iron and incidental impurities.
Description
_ 1 _ 20-18636 PRECIPITATION HARDENING FERRITIC-PEARLICTIC STEEL
The invention relates to a precipitation hardening ferritic-pearli-tic steel (AFP steel), especially as a material for gas change valves of internal combustion engines.
Gas valves are inlet and outlet valves in internal combustion en-gines which control the gas change in the engine and seal off the cylinder chamber.
The development of engines in the direction of increasingly high powers results in a constantly increasing thermal stressing of the valves, the outlet valves, around which hot combustion gases flow, reaching operating temperatures up to about 850 °C. In contrast, inlet valves are cooled by the carburated fuel and seldom reach temperatures above 550 °C.
Valve materials require not only high heat resistance properties, but also properties of use as shown diagrammatically in Fig. 1 (1).
For these properties special valve materials have been developed which are standardized by DIN 17480 (2). Three groups of materials can be distinguished:
- martensitic-carbidic steels, such as materials Nos. 1.4718, 1.4731, 1.4748 - austenitic-carbidic steels, some of them precipitation harden-able, such as materials Nos. 1.4873, 1.4875, 1.4882, 1.4785 and - austenitic-precipitation hardenable alloys, such as materials Nos. 2.4955, 2.4952.
The invention relates to a precipitation hardening ferritic-pearli-tic steel (AFP steel), especially as a material for gas change valves of internal combustion engines.
Gas valves are inlet and outlet valves in internal combustion en-gines which control the gas change in the engine and seal off the cylinder chamber.
The development of engines in the direction of increasingly high powers results in a constantly increasing thermal stressing of the valves, the outlet valves, around which hot combustion gases flow, reaching operating temperatures up to about 850 °C. In contrast, inlet valves are cooled by the carburated fuel and seldom reach temperatures above 550 °C.
Valve materials require not only high heat resistance properties, but also properties of use as shown diagrammatically in Fig. 1 (1).
For these properties special valve materials have been developed which are standardized by DIN 17480 (2). Three groups of materials can be distinguished:
- martensitic-carbidic steels, such as materials Nos. 1.4718, 1.4731, 1.4748 - austenitic-carbidic steels, some of them precipitation harden-able, such as materials Nos. 1.4873, 1.4875, 1.4882, 1.4785 and - austenitic-precipitation hardenable alloys, such as materials Nos. 2.4955, 2.4952.
When designing valves subjected to different loads, valve manufacturers take into account the different properties of the valve materials. For example, lightly-loaded inlet valves are frequently produced in the form of single-metal valves ("Monovalves") from steel 1.4718 (X 45 CrSi 93).
Hardened and tempered ground rods are, for instance, partially heated and hot-formed into a pear-shape. Then by drop forging the valve disc was formed followed by hardening and tempering or simply tempering and final machining. In the case of heavily stressed outlet valves, valve manufacturers are often obliged to combine valve materials appropriately with one another. As shown in Fig. 1 a bimetallic valve, for example, the high heat resistance and resistance to hot gas corrosion of precipitation hardenable austenitic steel can be combined with the high-wear resistance and the good sliding properties of hardenable martensitic steel can be combined by the friction welding of a valve disc of steel 1.4871 (X 53 CrMnNiN
219) with a steel 1.4718 (X 45 CrSi 93).
In the present state of the art more than half the total valve material requirements for inlet valves and lightly-stressed outlet valves, and also for the stems of inlet and outlet bimetallic valves, are met with steel 1.4718 (X 45 CrSi 93) or modifications. These steels are processed by steel and valve manufacturers in accordance with the main production sequences shown in Fig. 2 and 3.
It is an object of the invention to substitute the previously used martensitic carbidic steels, which in accordance with the production sequence must be subjected to several thermal treatments by both steel and valve manufacturers, by steels which achieve the required valve properties as far as possible without thermal treatment and are less expensive to shape by machining.
.", ..:
2a In accordance with one aspect of the present invention there is provided use of a precipitation-hardening ferritic-perlitic steel, comprising: 0.20 to 0.600 carbon; 0.20 to 0.950 silicon; 0.50 to 1.800 manganese; 0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium; and optionally up to 20% sulphur; up to 0.700 chromium.; up to O.lOo aluminium; up to 0.05% titanium, individually or in combination; the remainder iron and impurities associated with smelting, as a material for gas change valves in internal combustion engines.
In accordance with another aspect of the present invention there is provided a gas change valve for an internal combustion engine made with a precipitation-hardening ferritic-perlitic steel comprising: 0.20 to 0.600 carbon; 0.20 to 0.95% silicon; 0.50 to 1.80% manganese; 0.004 to 0.04%
nitrogen; 0.05 to 0.200 vanadium and/or niobium; and optionally up to 0.20% sulphur; up to 0.700 chromium; up to O.lOo aluminium; up to 0.05% titanium, individually or in combination; the remainder iron and impurities associated with smelting.
Hardened and tempered ground rods are, for instance, partially heated and hot-formed into a pear-shape. Then by drop forging the valve disc was formed followed by hardening and tempering or simply tempering and final machining. In the case of heavily stressed outlet valves, valve manufacturers are often obliged to combine valve materials appropriately with one another. As shown in Fig. 1 a bimetallic valve, for example, the high heat resistance and resistance to hot gas corrosion of precipitation hardenable austenitic steel can be combined with the high-wear resistance and the good sliding properties of hardenable martensitic steel can be combined by the friction welding of a valve disc of steel 1.4871 (X 53 CrMnNiN
219) with a steel 1.4718 (X 45 CrSi 93).
In the present state of the art more than half the total valve material requirements for inlet valves and lightly-stressed outlet valves, and also for the stems of inlet and outlet bimetallic valves, are met with steel 1.4718 (X 45 CrSi 93) or modifications. These steels are processed by steel and valve manufacturers in accordance with the main production sequences shown in Fig. 2 and 3.
It is an object of the invention to substitute the previously used martensitic carbidic steels, which in accordance with the production sequence must be subjected to several thermal treatments by both steel and valve manufacturers, by steels which achieve the required valve properties as far as possible without thermal treatment and are less expensive to shape by machining.
.", ..:
2a In accordance with one aspect of the present invention there is provided use of a precipitation-hardening ferritic-perlitic steel, comprising: 0.20 to 0.600 carbon; 0.20 to 0.950 silicon; 0.50 to 1.800 manganese; 0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium; and optionally up to 20% sulphur; up to 0.700 chromium.; up to O.lOo aluminium; up to 0.05% titanium, individually or in combination; the remainder iron and impurities associated with smelting, as a material for gas change valves in internal combustion engines.
In accordance with another aspect of the present invention there is provided a gas change valve for an internal combustion engine made with a precipitation-hardening ferritic-perlitic steel comprising: 0.20 to 0.600 carbon; 0.20 to 0.95% silicon; 0.50 to 1.80% manganese; 0.004 to 0.04%
nitrogen; 0.05 to 0.200 vanadium and/or niobium; and optionally up to 0.20% sulphur; up to 0.700 chromium; up to O.lOo aluminium; up to 0.05% titanium, individually or in combination; the remainder iron and impurities associated with smelting.
In the accompanying drawings:
Fig. 1 is an elevation of a friction-welded bimetallic outlet valve, showing the demands thereon;
Fig. 2 is a flow chart showing a steel manufacturer's main production sequences of martensitic-carbidic valve steel (example: X 45 CrSi 93) or other martensitic valve steels (prior art);
Fig. 3 is a valve manufacturer's main production sequences of martensitic-carbidic valve steel (example:
X 45 CrSi 93) or other martensitic valve steel (prior art);
Fig. 4 shows a collection of graphs disclosing various properties of steel A and steel B, steel A being 1.4718 (17.5 mm diameter, standard hardening and tempering), steel B being AFP steel (condition as delivered [BY/drawn/ground], 9.32 mm diameter);
Fig. 5 shows various graphs relating to duration of stressing for steels A and B, these steels being the same as those in Fig. 4;
Fig. 6 is a flow sheet showing a steel manufacturers main production sequences of AFP steels for gas valves of internal combustion engines (according to the invention) Fig. 7 is a flow sheet showing a valve manufacturer's main production sequences of AFP steels for gas shutter valves of internal combustion engines (according to the invention).
Fig. 1 is an elevation of a friction-welded bimetallic outlet valve, showing the demands thereon;
Fig. 2 is a flow chart showing a steel manufacturer's main production sequences of martensitic-carbidic valve steel (example: X 45 CrSi 93) or other martensitic valve steels (prior art);
Fig. 3 is a valve manufacturer's main production sequences of martensitic-carbidic valve steel (example:
X 45 CrSi 93) or other martensitic valve steel (prior art);
Fig. 4 shows a collection of graphs disclosing various properties of steel A and steel B, steel A being 1.4718 (17.5 mm diameter, standard hardening and tempering), steel B being AFP steel (condition as delivered [BY/drawn/ground], 9.32 mm diameter);
Fig. 5 shows various graphs relating to duration of stressing for steels A and B, these steels being the same as those in Fig. 4;
Fig. 6 is a flow sheet showing a steel manufacturers main production sequences of AFP steels for gas valves of internal combustion engines (according to the invention) Fig. 7 is a flow sheet showing a valve manufacturer's main production sequences of AFP steels for gas shutter valves of internal combustion engines (according to the invention).
It was found that both after rolling into wire and also after upsetting or forging with cooling from hot shaping temperature in air ("BY condition") AFP steels have mechanica-technological values which are comparable with those of steel 1.4718. Table 1 shows the chemical composition, while Table 2 and Fig. 4 show the strength properties at room temperature and elevated temperatures. Table 3 and Fig. 5 characterize the creep rupture strength of the comparison materials 1.4718 (X 45 CrSi 93) and an AFP steel and show that in the BY
condition AFP steels are a sensible alternative to the prior art steel 1.4718.
condition AFP steels are a sensible alternative to the prior art steel 1.4718.
Table 1 Comparison steels: 1.4718 (X 45 CrSi 93) and AFP steel chemical composition - melt analyses: (values in % by weight) Steel 1.4718 AFP-steel A B
C 0.44 0.43 Si 2.78 0.66 Mn 0.32 1.38 P 0.015 0.006 S 0.003 0.027 Cr 8.93 0.15 Mo 0.12 0.02 Ni 0.20 0.08 V 0.03 0.12 W 0.02 < 0.01 A1 0.027 0.047 B - < 0.004 Co 0.06 0.008 Cu 0.04 0.10 N 0.018 0.016 Nb < 0.005 < 0.005 Ti < 0.003 < 0.003 Sn < 0.003 0.012 As 0.008 0.010 Table 2 Comparison steels: 1.4718 (X 45 CrSi 93) and AFP steel Strength properties at room temperature and elevated temperatures A = 1.4718; 17.5 mm diameter; standard hardening and tempering;
B = AFP steel; BY/drawn/ground 9.32 mm diameter Steel Testing RP 0.2 RP 1.0 F~ RP 0.2 A5 Z
Temperature Rm ° C N/mm2 N/mm2 N/mmZ % o 20 899 959 1098 0.93 18.0 53.5 A 450 611 708 776 0.78 26.8 76.0 1.4718 500 472 584 638 0.74 34.0 84.0 550 344 440 510 0.67 38.3 90.1 20 876 - 1069 0.82 14.5 54.0 B 450 564 651 681 0.83 ~~ 72.0 AFP-steel 500 433 529 536 0.81 ~~ 70.0 550 337 399 400 0.84 ~~ 70.0 ~~ breakage outside the measuring mark tone _ 7 _ Table 3 Comparison steels: 1.4718 (X 45 CrSi 93) and AFP steel Creep rupture strength at 450, 500 and 550°C for 102 and 103 hours duration of stressing A = 1.4718; 17.5 mm diameter; standard hardening and tempering;
B = AFP steel; BY/drawn/ground D = steel 9.32 mm diameter 1.4718 550 210 130 AFP-steel 550 140 70 _ 8 _ 2018636 After upsetting and die-forging, the inlet valves produced by a valve manufacturer from AFP steels according to the invention were cooled in air and tested in engines without any further heat treatment.
The results obtained are also positive and adequate in comparison with the stell 1.4718 previously used.
Steels according to the invention have the advantage over the pre-viously used materials for gas valves that they can be produced easily on an economical basis in the sequences shown in Figs. 6 and 7.
By a comparison between the sequences and the prior art main pro-duction sequences shown in Figs. 2 and 3 it can be seen that AFP
steels do not need thermal treatments in contrast to known valve steels.
Another advantage is that due to the lower sensitivity of the AFP
steels to cracking and decarburization in comparison with the w 9 _ known valve steel 1.4718, and also due to the absence of decarbu-rization through the elimination of thermal treatments, the 100 ~
smooth grinding of the semi-finished product for further rolling at present required by steel 1.4718 is replaced by partial grinding in the case of the AFP steels.
Moreover, the amount of machining for the centerless grinding of rod steel can be reduced or even completely eliminated, if drawn rods are substituted for ground rods in the production of gas valves from AFP steels.
In addition to lower sensitivity to cracking and decarburization, the AFP steels have the following further advantages over martensi-tic carbidic valve steels:
less expensive alloying costs, improved continuous castability, . lower sensitivity to coarse-grained recrystallization, improved machinability.
As a whole, these advantages mean that the use of the AFP steels for gas valves of internal combustion engines represents a substantial saving in costs to both steel producers and valve manufacturers.
Bibliography 1) V. Schuler, T. Kreul, S. Engineer: "Special Quality Constructional Steels in Motorcars", Thyssen Technische Berichte 2 (1986), pages 233-240 2) DIN 17480:"Valve Materials", Beuth Verlag GmbH, Berlin 30 (September 1984)
C 0.44 0.43 Si 2.78 0.66 Mn 0.32 1.38 P 0.015 0.006 S 0.003 0.027 Cr 8.93 0.15 Mo 0.12 0.02 Ni 0.20 0.08 V 0.03 0.12 W 0.02 < 0.01 A1 0.027 0.047 B - < 0.004 Co 0.06 0.008 Cu 0.04 0.10 N 0.018 0.016 Nb < 0.005 < 0.005 Ti < 0.003 < 0.003 Sn < 0.003 0.012 As 0.008 0.010 Table 2 Comparison steels: 1.4718 (X 45 CrSi 93) and AFP steel Strength properties at room temperature and elevated temperatures A = 1.4718; 17.5 mm diameter; standard hardening and tempering;
B = AFP steel; BY/drawn/ground 9.32 mm diameter Steel Testing RP 0.2 RP 1.0 F~ RP 0.2 A5 Z
Temperature Rm ° C N/mm2 N/mm2 N/mmZ % o 20 899 959 1098 0.93 18.0 53.5 A 450 611 708 776 0.78 26.8 76.0 1.4718 500 472 584 638 0.74 34.0 84.0 550 344 440 510 0.67 38.3 90.1 20 876 - 1069 0.82 14.5 54.0 B 450 564 651 681 0.83 ~~ 72.0 AFP-steel 500 433 529 536 0.81 ~~ 70.0 550 337 399 400 0.84 ~~ 70.0 ~~ breakage outside the measuring mark tone _ 7 _ Table 3 Comparison steels: 1.4718 (X 45 CrSi 93) and AFP steel Creep rupture strength at 450, 500 and 550°C for 102 and 103 hours duration of stressing A = 1.4718; 17.5 mm diameter; standard hardening and tempering;
B = AFP steel; BY/drawn/ground D = steel 9.32 mm diameter 1.4718 550 210 130 AFP-steel 550 140 70 _ 8 _ 2018636 After upsetting and die-forging, the inlet valves produced by a valve manufacturer from AFP steels according to the invention were cooled in air and tested in engines without any further heat treatment.
The results obtained are also positive and adequate in comparison with the stell 1.4718 previously used.
Steels according to the invention have the advantage over the pre-viously used materials for gas valves that they can be produced easily on an economical basis in the sequences shown in Figs. 6 and 7.
By a comparison between the sequences and the prior art main pro-duction sequences shown in Figs. 2 and 3 it can be seen that AFP
steels do not need thermal treatments in contrast to known valve steels.
Another advantage is that due to the lower sensitivity of the AFP
steels to cracking and decarburization in comparison with the w 9 _ known valve steel 1.4718, and also due to the absence of decarbu-rization through the elimination of thermal treatments, the 100 ~
smooth grinding of the semi-finished product for further rolling at present required by steel 1.4718 is replaced by partial grinding in the case of the AFP steels.
Moreover, the amount of machining for the centerless grinding of rod steel can be reduced or even completely eliminated, if drawn rods are substituted for ground rods in the production of gas valves from AFP steels.
In addition to lower sensitivity to cracking and decarburization, the AFP steels have the following further advantages over martensi-tic carbidic valve steels:
less expensive alloying costs, improved continuous castability, . lower sensitivity to coarse-grained recrystallization, improved machinability.
As a whole, these advantages mean that the use of the AFP steels for gas valves of internal combustion engines represents a substantial saving in costs to both steel producers and valve manufacturers.
Bibliography 1) V. Schuler, T. Kreul, S. Engineer: "Special Quality Constructional Steels in Motorcars", Thyssen Technische Berichte 2 (1986), pages 233-240 2) DIN 17480:"Valve Materials", Beuth Verlag GmbH, Berlin 30 (September 1984)
Claims (4)
1. Use of a precipitation-hardening ferritic-perlitic steel, comprising:
0.20 to 0.60% carbon;
0.20 to 0.95% silicon;
0.50 to 1.80% manganese;
0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium;
and optionally up to 0.20% sulphur;
up to 0.70% chromium;
up to 0.10% aluminium;
up to 0.05% titanium, individually or in combination;
the remainder iron and impurities associated with smelting, as a material for gas change valves in internal combustion engines.
0.20 to 0.60% carbon;
0.20 to 0.95% silicon;
0.50 to 1.80% manganese;
0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium;
and optionally up to 0.20% sulphur;
up to 0.70% chromium;
up to 0.10% aluminium;
up to 0.05% titanium, individually or in combination;
the remainder iron and impurities associated with smelting, as a material for gas change valves in internal combustion engines.
2. Use according to claim 1, wherein the steel comprises:
0.35 to 0.50% carbon;
0.40 to 0.80% silicon;
1.00 to 1.60% manganese;
0.05 to 0.50% chromium;
0.01 to 0.05% aluminium;
0.008 to 0.03% nitrogen;
0.05 to 0.12% vanadium;
and the remainder iron and impurities associated with smelting.
0.35 to 0.50% carbon;
0.40 to 0.80% silicon;
1.00 to 1.60% manganese;
0.05 to 0.50% chromium;
0.01 to 0.05% aluminium;
0.008 to 0.03% nitrogen;
0.05 to 0.12% vanadium;
and the remainder iron and impurities associated with smelting.
3. Use according to claim 2, wherein the steel additionally comprises up to 0.05% sulphur, up to 0.05% niobium, and up to 0.025% titanium, individually or in combination.
4. A gas change valve for an internal combustion engine made with a precipitation-hardening ferritic-perlitic steel comprising:
0.20 to 0.60% carbon;
0.20 to 0.95% silicon;
0.50 to 1.80% manganese;
0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium;
and optionally up to 0.20% sulphur;
up to 0.70% chromium;
up to 0.10% aluminium;
up to 0.05% titanium, individually or in combination;
the remainder iron and impurities associated with smelting.
0.20 to 0.60% carbon;
0.20 to 0.95% silicon;
0.50 to 1.80% manganese;
0.004 to 0.04% nitrogen;
0.05 to 0.20% vanadium and/or niobium;
and optionally up to 0.20% sulphur;
up to 0.70% chromium;
up to 0.10% aluminium;
up to 0.05% titanium, individually or in combination;
the remainder iron and impurities associated with smelting.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE3918869 | 1989-06-09 | ||
| DEP3918869.8 | 1989-06-09 | ||
| DE4014072A DE4014072A1 (en) | 1989-06-09 | 1990-05-02 | USE OF ELIGIBLE FERRITIC-PERLITIC (AFP) STEELS AS A MATERIAL FOR GAS EXCHANGE VALVES OF COMBUSTION ENGINES |
| DEP4014072.9 | 1990-05-02 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2018636A1 CA2018636A1 (en) | 1990-12-09 |
| CA2018636C true CA2018636C (en) | 2000-10-24 |
Family
ID=25881758
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002018636A Expired - Lifetime CA2018636C (en) | 1989-06-09 | 1990-06-08 | Precipitation hardening ferritic-pearlitic steel |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0411282B1 (en) |
| JP (1) | JP2820776B2 (en) |
| KR (1) | KR0151154B1 (en) |
| CA (1) | CA2018636C (en) |
| DE (2) | DE4014072A1 (en) |
| ES (1) | ES2045652T3 (en) |
| FI (1) | FI96327C (en) |
Families Citing this family (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4109628C2 (en) * | 1990-07-12 | 1997-04-17 | Mahle Gmbh | Use of a precipitation hardening ferritic pearlitic steel |
| DE4137240A1 (en) * | 1991-11-13 | 1993-05-19 | Thyssen Edelstahlwerke Ag | AFP steel used for prodn. of large forged tools - has low sulphur content and uniformly high tensile strength through tempering |
| DE4341811A1 (en) * | 1993-12-08 | 1995-06-14 | Man B & W Diesel Ag | Gas exchange valve for an internal combustion engine |
| DE4343565C1 (en) * | 1993-12-21 | 1995-06-08 | Ver Schmiedewerke Gmbh | Method for producing rail wheels and rail wheel parts |
| DE4406896C1 (en) * | 1994-03-03 | 1995-06-29 | Daimler Benz Ag | Martensitic age-hardening process for esp. alloyed steel inlet valves |
| DE19618477C2 (en) * | 1996-05-08 | 2000-08-03 | Trw Deutschland Gmbh | Manufacturing process for a nitrided bimetal valve |
| DE10029299C2 (en) * | 2000-06-14 | 2003-03-27 | Daimler Chrysler Ag | Multi-part assembled valve for reciprocating engines |
| DE10031927A1 (en) * | 2000-06-30 | 2002-01-24 | Daimler Chrysler Ag | Multi-part valve, for an IC motor, has a lightweight valve head bonded to a lightweight valve shaft by friction welding using low-cost components giving high thermal and mechanical resistance |
| DE10037132A1 (en) * | 2000-07-31 | 2002-02-14 | Volkswagen Ag | Production of a plate valve used as an inlet and outlet valve of an I.C. engine comprises connecting a sintered valve head of a plate valve with the valve shaft using a welding process |
| DE102007021101A1 (en) * | 2007-05-03 | 2008-11-06 | Mahle International Gmbh | Alloy steel and its use |
| DE102007026018B4 (en) | 2007-06-04 | 2023-01-19 | Scania Cv Ab | Bimetallic valve with a truncated cone-shaped area of the valve stem |
| DE102008061237A1 (en) * | 2008-12-09 | 2010-06-10 | Man Diesel Se | Gas exchange valve and method for its production |
| DE102013210897A1 (en) * | 2013-06-11 | 2014-12-11 | Mahle International Gmbh | Method for producing a built-up hollow valve of an internal combustion engine |
| CN107514316A (en) * | 2015-05-18 | 2017-12-26 | 夏志清 | A kind of diesel engine cylinder head |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| BE619810A (en) * | 1961-07-05 | 1962-11-05 | Trafikaktiebolaget Graengesber | Improvements to a process for alloying steel, steel produced by the process and arrangement for carrying out the process |
| GB1101193A (en) * | 1966-01-21 | 1968-01-31 | United Steel Companies Ltd | Steel |
| US3846184A (en) * | 1968-08-06 | 1974-11-05 | Bethlehem Steel Corp | Wear resistant steel |
| US3562028A (en) * | 1968-08-28 | 1971-02-09 | Inland Steel Co | Tough,high strength steel article |
| JPS5845354A (en) * | 1981-09-10 | 1983-03-16 | Daido Steel Co Ltd | Case hardening steel |
| JPS62274051A (en) * | 1986-05-21 | 1987-11-28 | Kobe Steel Ltd | Steel excellent in fatigue resistance and sag resistance and steel wire for valve spring using same |
| DE3719569C2 (en) * | 1986-07-05 | 1988-06-23 | Thyssen Edelstahlwerke Ag | Microalloyed steels. |
| JPS6468424A (en) * | 1987-09-07 | 1989-03-14 | Kobe Steel Ltd | Production of high-toughness non-tempered hot forging having excellent fatigue resistance and machinability |
-
1990
- 1990-05-02 DE DE4014072A patent/DE4014072A1/en active Granted
- 1990-06-08 EP EP90110888A patent/EP0411282B1/en not_active Expired - Lifetime
- 1990-06-08 ES ES90110888T patent/ES2045652T3/en not_active Expired - Lifetime
- 1990-06-08 CA CA002018636A patent/CA2018636C/en not_active Expired - Lifetime
- 1990-06-08 DE DE90110888T patent/DE59002456D1/en not_active Expired - Lifetime
- 1990-06-09 KR KR1019900008591A patent/KR0151154B1/en not_active IP Right Cessation
- 1990-06-11 JP JP2152484A patent/JP2820776B2/en not_active Expired - Lifetime
- 1990-06-11 FI FI902899A patent/FI96327C/en active IP Right Grant
Also Published As
| Publication number | Publication date |
|---|---|
| KR0151154B1 (en) | 1998-11-16 |
| ES2045652T3 (en) | 1994-01-16 |
| CA2018636A1 (en) | 1990-12-09 |
| JP2820776B2 (en) | 1998-11-05 |
| DE59002456D1 (en) | 1993-09-30 |
| DE4014072C2 (en) | 1991-12-05 |
| KR910001081A (en) | 1991-01-30 |
| JPH03219045A (en) | 1991-09-26 |
| FI902899A0 (en) | 1990-06-11 |
| FI96327C (en) | 1996-06-10 |
| DE4014072A1 (en) | 1990-12-20 |
| FI96327B (en) | 1996-02-29 |
| EP0411282A3 (en) | 1991-07-31 |
| EP0411282B1 (en) | 1993-08-25 |
| EP0411282A2 (en) | 1991-02-06 |
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