EP0003208A1 - Silicon alloyed steel - Google Patents
Silicon alloyed steel Download PDFInfo
- Publication number
- EP0003208A1 EP0003208A1 EP79850001A EP79850001A EP0003208A1 EP 0003208 A1 EP0003208 A1 EP 0003208A1 EP 79850001 A EP79850001 A EP 79850001A EP 79850001 A EP79850001 A EP 79850001A EP 0003208 A1 EP0003208 A1 EP 0003208A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- heat treatment
- microstructure
- residual austenite
- steel according
- 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.)
- Ceased
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 35
- 239000010959 steel Substances 0.000 title claims abstract description 35
- 229910052710 silicon Inorganic materials 0.000 title description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 title description 4
- 239000010703 silicon Substances 0.000 title description 4
- 238000005275 alloying Methods 0.000 claims abstract description 15
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract 4
- 239000012535 impurity Substances 0.000 claims abstract 2
- 229910052742 iron Inorganic materials 0.000 claims abstract 2
- 229910001566 austenite Inorganic materials 0.000 claims description 19
- 229910001563 bainite Inorganic materials 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 229910000617 Mangalloy Inorganic materials 0.000 description 3
- 238000000354 decomposition reaction Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910000677 High-carbon steel Inorganic materials 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000011651 chromium Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- FXNGWBDIVIGISM-UHFFFAOYSA-N methylidynechromium Chemical compound [Cr]#[C] FXNGWBDIVIGISM-UHFFFAOYSA-N 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
Definitions
- the present invention relates to an Si-alloyed high carbon steel, which by isothermal heat treatment obtains particularly advantageous strength and toughness properties and which is useful especially in wearing parts subjected to heavy impacts.
- Mn-alloyed austenitic steel so-called Hadfield steel
- toughness is required of the part.
- High carbon chromium steels are brittle and their workability is poor. They are also expensive due to high alloy content.
- the advantageous mechanical properties of the steel according to the present invention are based on the bainitic-austenitic dual-phase microstructure obtained in the isothermal heat treatment.
- the bainitic component of the microstructure gives the steel good initial hardness and rich residual austenite gives it strong strain hardening capacity.
- silicon as an alloying element is known e.g. in spring steels wherein C- and Si-contents are generally C ⁇ 0.8 %, Si ⁇ 2.0 %. In these steels, Si-alloying is generally used as an alloying element increasing hardenability and tempering resistance.
- the carbon content of a steel is 1.0 % and it decomposes to 50 % bainite without carbide formation, the carbon content of residual austenite increases to appr. 2 %.
- the composition (C- and Si-content) of the steel, decomposition temperature and holding time it is possible to control the bainite-austenite ratio obtained as a result of the decomposition of austenite.
- test steels were heat treated as follows: austenitizing 920 - 1030°C, 10 min. + isothermal bainitizing at 380°C, 350°C or 320°C, water cooling.
- the test specimen were subjected to tensile tests performed with an 0 8 mm tensile test specimen, to impact tests (KV) and residual austenite content was determined with X-ray measurements. Test results are illustrated in Table II.
- the yield strength will be R p 0.2 > 850 N/mm and the tensile strength R > 1300 N/mm2 when the isothermal bainitizing temperature T B is 380°C. Lowering the bainitizing temperature below 350°C increases the strength of the steel considerably. The bainitizing time will then be longer and the microstructure obtained is lower bainite. Elongation to fracture A 5 > 20 %. Too low a C + Si-content leads to a too small amount of residual austenite with the stronger but more brittle bainite controlling the properties. This is the case with the example steel 1.
- C + Si must be ⁇ 2.80. Too high a C + Si-content, on the other hand, leads to a too high residual austenite content. Thus, the residual austenite is too much in control of mechanical properties, the strength thus remaining lower. Thus, the residual austenite is also mechanically more unstable which impairs the elongation to fracture. This is the case with the example steel 4. Thus, C + Si must be ⁇ 3.5.
- the elongation to fracture A 5 is 30 - 40 % and consists mainly of uniform elongation which is an indication of strain hardening capacity found only in austenitic Hadfield manganese steel and stainless steels.
- yield strength of both of these steels is ⁇ 50 % of the yield strength of the steel of the present invention.
- the steel according to the invention can be alloyed with austenite stabilizing alloying elements, such as manganese and nickel, up to appr. 1 %.
- austenite stabilizing alloying elements such as manganese and nickel
- carbide forming chromium and niobium can be used in alloying.
- the former improves hardenability on large bar diameters and it can be used in amounts ⁇ 1 %, preferably ⁇ 0.5 %.
- Niobium on the other hand, can be used to control grain growth properties.
- the alloying amount needed for this is ⁇ 0.1 %.
- Al-alloying is preferable for binding of free nitrogen in ferritic bainite which is advantageous for toughness, particularly at low temperatures.
- the alloying amount needed for this is 0.1 %.
- the steel according to the invention has produced a combination of strength and toughness properties that has been impossible to obtain with prior art steels. Moreover, since these properties are achieved by simple isothermal heat treatment and inexpensive alloying, the steel according to the invention can be expected to receive wide acceptance and to be widely used in applications requiring high strength and good abrasion resistance.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Laminated Bodies (AREA)
Abstract
This invention is related to a high strength steel provided with a bainitic-austenitic microstructure which is accomplished by isothermal heat treatment. Said steel contains various alloying elements in the following amounts expressed as weight percentage:
the remainder consisting of iron and normal impurities.
Description
- The present invention relates to an Si-alloyed high carbon steel, which by isothermal heat treatment obtains particularly advantageous strength and toughness properties and which is useful especially in wearing parts subjected to heavy impacts.
- For such wearing parts it is generally known to use Mn-alloyed austenitic steel, so-called Hadfield steel, when, in addition to abrasion resistance, toughness is required of the part.
- If toughness is not necessary it is possible to use e.g. high carbon chromium alloyed steels (1.0 % C, 12 % Cr). Both such steels have several drawbacks. Hadfield steel (1.0 % C, 13 % Mn) is difficult to manufacture, it can only be formed by casting and its corrosion resistance and weldability are poor. Due to the high Mn-alloy content this steel is also expensive.
- High carbon chromium steels, on the other hand, are brittle and their workability is poor. They are also expensive due to high alloy content.
- The advantageous mechanical properties of the steel according to the present invention are based on the bainitic-austenitic dual-phase microstructure obtained in the isothermal heat treatment. The bainitic component of the microstructure gives the steel good initial hardness and rich residual austenite gives it strong strain hardening capacity.
- The chemical composition figures stated in the following are based on the weight.
- In the present steel, advantage has been taken of a known effect of silicon to prevent carbide formation. By increasing the silicon content of a high carbon steel up to 2.0 - 3.0 %, carbide formation can be prevented during isothermal decomposition of austenite at a suitable temperature.
- The use of silicon as an alloying element is known e.g. in spring steels wherein C- and Si-contents are generally C < 0.8 %, Si < 2.0 %. In these steels, Si-alloying is generally used as an alloying element increasing hardenability and tempering resistance.
- Commonly known are also low carbon high Si-alloyed steels (C < 0.1 %, Si- 2.0 - 4.0 %) which are used as core plates of electromagnets. The purpose of Si-alloying is to prevent the formation of carbide (cementite), when after the austenitizing the steel is allowed to decompose isothermally to upper bainite within a temperature range of 350 - 450°C or to lower bainite within the temperature range of 280 - 350°C. Thus, the obtained bainitic ferrite only contains ~0.01 % of carbon. With carbide formation prevented, carbon must diffuse into the remaining austenite as the bainite reaction proceeds. This, on the other hand, increases the stability of austenite with increasing carbon content. If for example the carbon content of a steel is 1.0 % and it decomposes to 50 % bainite without carbide formation, the carbon content of residual austenite increases to appr. 2 %. Thus, by controlling the composition (C- and Si-content) of the steel, decomposition temperature and holding time, it is possible to control the bainite-austenite ratio obtained as a result of the decomposition of austenite.
- The following examples illustrate mechanical properties obtained with the steel according to the invention.
- The chemical compositions of the example steels are presented in Table I.
- The test steels were heat treated as follows: austenitizing 920 - 1030°C, 10 min. + isothermal bainitizing at 380°C, 350°C or 320°C, water cooling. The test specimen were subjected to tensile tests performed with an 0 8 mm tensile test specimen, to impact tests (KV) and residual austenite content was determined with X-ray measurements. Test results are illustrated in Table II.
- By comparing the strength and toughness values obtained with residual austenite contents, it can be seen that the best combinations of properties are accomplished with the residual austenite content between 30 and 40 %. Thus, the yield strength will be Rp 0.2 > 850 N/mm and the tensile strength R > 1300 N/mm2 when the isothermal bainitizing temperature TB is 380°C. Lowering the bainitizing temperature below 350°C increases the strength of the steel considerably. The bainitizing time will then be longer and the microstructure obtained is lower bainite. Elongation to fracture A5 > 20 %. Too low a C + Si-content leads to a too small amount of residual austenite with the stronger but more brittle bainite controlling the properties. This is the case with the example steel 1. Thus, C + Si must be ≥ 2.80. Too high a C + Si-content, on the other hand, leads to a too high residual austenite content. Thus, the residual austenite is too much in control of mechanical properties, the strength thus remaining lower. Thus, the residual austenite is also mechanically more unstable which impairs the elongation to fracture. This is the case with the example steel 4. Thus, C + Si must be ≤ 3.5.
- According to the test results, the most suitable range for the sum is C + Si = 2.90 - 3.40 %, however with C ≥ 0.8 % and Si ≥ 2.0 %. Thus, the elongation to fracture A5 is 30 - 40 % and consists mainly of uniform elongation which is an indication of strain hardening capacity found only in austenitic Hadfield manganese steel and stainless steels. However, in unworked condition, yield strength of both of these steels is ≤ 50 % of the yield strength of the steel of the present invention.
- In order to improve its heat treatment properties, the steel according to the invention can be alloyed with austenite stabilizing alloying elements, such as manganese and nickel, up to appr. 1 %. Thus, for the C-content, it is necessary to take into account the effect of the additional alloying on the stability of austenite. Also carbide forming chromium and niobium can be used in alloying. The former improves hardenability on large bar diameters and it can be used in amounts ≤ 1 %, preferably ≤ 0.5 %. Niobium, on the other hand, can be used to control grain growth properties. The alloying amount needed for this is ≤ 0.1 %. Al-alloying is preferable for binding of free nitrogen in ferritic bainite which is advantageous for toughness, particularly at low temperatures. The alloying amount needed for this is 0.1 %.
- The steel according to the invention has produced a combination of strength and toughness properties that has been impossible to obtain with prior art steels. Moreover, since these properties are achieved by simple isothermal heat treatment and inexpensive alloying, the steel according to the invention can be expected to receive wide acceptance and to be widely used in applications requiring high strength and good abrasion resistance.
Claims (6)
1. High strength steel provided with a bainitic-austenitic microstructure which is accomplished by isothermal heat treatment, characterized in that the steel contains various alloying elements in the following amounts expressed as weight percentage:
the remainder consisting of iron and normal impurities.
2. Steel according to claim 1, wherein the alloying sum C + Si = 2.9 - 3.4 %.
3. Steel according to claim 1 or 2,
characterized in that it contains one or more of the following alloying elements with the following contents:
characterized in that it contains one or more of the following alloying elements with the following contents:
4. Steel according to claim 1, 2 or 3,
characterized in that it has been provided with a dual-phase microstructure produced by isothermal heat treatment carried out at a temperature of 350 - 450oC, the microstructure mainly consisting of upper bainite and residual austenite and wherein the proportion of residual austenite is 30 - 40 % by volume.
characterized in that it has been provided with a dual-phase microstructure produced by isothermal heat treatment carried out at a temperature of 350 - 450oC, the microstructure mainly consisting of upper bainite and residual austenite and wherein the proportion of residual austenite is 30 - 40 % by volume.
5. Steel according to claim 1, 2 or 3,
characterized in that it contains a dual-phase microstructure obtained by isothermal heat treatment carried out at a temperature of 280 - 350°C the microstructure mainly consisting of lower bainite and wherein the proportion of residual austenite is 30 - 40 %.
characterized in that it contains a dual-phase microstructure obtained by isothermal heat treatment carried out at a temperature of 280 - 350°C the microstructure mainly consisting of lower bainite and wherein the proportion of residual austenite is 30 - 40 %.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FI780026A FI780026A (en) | 1978-01-05 | 1978-01-05 | KISELLEGERAT STAOL |
| FI780026 | 1978-01-05 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| EP0003208A1 true EP0003208A1 (en) | 1979-07-25 |
Family
ID=8511375
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP79850001A Ceased EP0003208A1 (en) | 1978-01-05 | 1979-01-04 | Silicon alloyed steel |
Country Status (6)
| Country | Link |
|---|---|
| EP (1) | EP0003208A1 (en) |
| CA (1) | CA1130617A (en) |
| DK (1) | DK583778A (en) |
| FI (1) | FI780026A (en) |
| IT (1) | IT1110730B (en) |
| NO (1) | NO790013L (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008019717A1 (en) * | 2006-08-17 | 2008-02-21 | Federal-Mogul Burscheid Gmbh | Steel material having a high silicon content for producing piston rings and cylinder sleeves |
| GB2462197A (en) * | 2008-07-31 | 2010-02-03 | Secr Defence | A super bainite steel |
| EP2235227A1 (en) * | 2007-12-06 | 2010-10-06 | Posco | High carbon steel sheet superior in tensile strength and elongation and method for manufacturing the same |
| WO2011023988A3 (en) * | 2009-08-24 | 2011-06-30 | The Secretary Of State For Defence | Armour |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1924099A (en) * | 1931-11-20 | 1933-08-29 | United States Steel Corp | Thermally hardening steel |
| CH311324A (en) * | 1952-03-12 | 1955-11-30 | Gussstahlwerk Witten Aktienges | Process for producing a workpiece from a steel alloy. |
| FR1286077A (en) * | 1961-01-20 | 1962-03-02 | Renault | Steel and treatment to obtain parts with a high thermal expansion coefficient |
| US3528088A (en) * | 1967-01-23 | 1970-09-08 | Hilti Ag | Anchoring device of spring steel and method for imparting the device with a bainitic structure |
| DE2334992A1 (en) * | 1972-07-12 | 1974-02-07 | Kymin Oy Kymmene Ab | ALLOY CAST IRON WITH BALL GRAPHITE |
-
1978
- 1978-01-05 FI FI780026A patent/FI780026A/en unknown
- 1978-12-28 DK DK583778A patent/DK583778A/en not_active Application Discontinuation
-
1979
- 1979-01-03 NO NO790013A patent/NO790013L/en unknown
- 1979-01-04 EP EP79850001A patent/EP0003208A1/en not_active Ceased
- 1979-01-04 CA CA319,150A patent/CA1130617A/en not_active Expired
- 1979-01-05 IT IT19100/79A patent/IT1110730B/en active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1924099A (en) * | 1931-11-20 | 1933-08-29 | United States Steel Corp | Thermally hardening steel |
| CH311324A (en) * | 1952-03-12 | 1955-11-30 | Gussstahlwerk Witten Aktienges | Process for producing a workpiece from a steel alloy. |
| FR1286077A (en) * | 1961-01-20 | 1962-03-02 | Renault | Steel and treatment to obtain parts with a high thermal expansion coefficient |
| US3528088A (en) * | 1967-01-23 | 1970-09-08 | Hilti Ag | Anchoring device of spring steel and method for imparting the device with a bainitic structure |
| DE2334992A1 (en) * | 1972-07-12 | 1974-02-07 | Kymin Oy Kymmene Ab | ALLOY CAST IRON WITH BALL GRAPHITE |
Non-Patent Citations (1)
| Title |
|---|
| ARCHIV EISENH]TTENWESEN, Vol. 45, No. 9, 1974, D}sseldorf. H. SEILSTORFER et al: "Umwandlungsverhalten in der Zwischenstufe und EinfluB der Umwandlung auf die mechanischen Eigenschaften von Stahl 71 Si 7", pages 623 to 627. * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008019717A1 (en) * | 2006-08-17 | 2008-02-21 | Federal-Mogul Burscheid Gmbh | Steel material having a high silicon content for producing piston rings and cylinder sleeves |
| EP2235227A1 (en) * | 2007-12-06 | 2010-10-06 | Posco | High carbon steel sheet superior in tensile strength and elongation and method for manufacturing the same |
| US20100307641A1 (en) * | 2007-12-06 | 2010-12-09 | Posco | High Carbon Steel Sheet Superior in Tensile Strength and Elongation and Method for Manufacturing the Same |
| US8465601B2 (en) * | 2007-12-06 | 2013-06-18 | Posco | High carbon steel sheet superior in tensile strength and elongation and method for manufacturing the same |
| EP2235227A4 (en) * | 2007-12-06 | 2014-07-02 | Posco | High carbon steel sheet superior in tensile strength and elongation and method for manufacturing the same |
| GB2462197A (en) * | 2008-07-31 | 2010-02-03 | Secr Defence | A super bainite steel |
| GB2462197B (en) * | 2008-07-31 | 2010-09-22 | Secr Defence | Bainite steel and methods of manufacture thereof |
| US8956470B2 (en) | 2008-07-31 | 2015-02-17 | The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland | Bainite steel and methods of manufacture thereof |
| WO2011023988A3 (en) * | 2009-08-24 | 2011-06-30 | The Secretary Of State For Defence | Armour |
| GB2485107A (en) * | 2009-08-24 | 2012-05-02 | Secr Defence | Armour |
Also Published As
| Publication number | Publication date |
|---|---|
| FI780026A (en) | 1979-07-06 |
| NO790013L (en) | 1979-07-06 |
| IT7919100A0 (en) | 1979-01-05 |
| IT1110730B (en) | 1986-01-06 |
| CA1130617A (en) | 1982-08-31 |
| DK583778A (en) | 1979-07-06 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| 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 |
|
| AK | Designated contracting states |
Designated state(s): BE CH DE FR GB NL SE |
|
| 17P | Request for examination filed | ||
| STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION HAS BEEN REFUSED |
|
| 18R | Application refused |
Effective date: 19820511 |
|
| RIN1 | Information on inventor provided before grant (corrected) |
Inventor name: NEVALAINEN, HARRI |