DK155053B - BAINITABLE, HIGH-STRENGTH TRANSFORMATION STEEL Alloy AND PREPARATION METHOD - Google Patents
BAINITABLE, HIGH-STRENGTH TRANSFORMATION STEEL Alloy AND PREPARATION METHOD Download PDFInfo
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- DK155053B DK155053B DK162779AA DK162779A DK155053B DK 155053 B DK155053 B DK 155053B DK 162779A A DK162779A A DK 162779AA DK 162779 A DK162779 A DK 162779A DK 155053 B DK155053 B DK 155053B
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- 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
- C22C38/12—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Control Of Heat Treatment Processes (AREA)
Description
iin
DK 155053 BDK 155053 B
Opfindelsen angår stål legeringer med høj sejhed og styrke samt en fremgangsmåde til fremstilling af genstande med disse egenskaber .The invention relates to high alloy toughness and strength steel alloys and to a process for making articles having these properties.
5 Det er kendt at fremstille stållegeringer, som samtidigt har høj sejhed og styrke, ved at anvende større mængder af værdifulde legeringstilsatsmaterialer. På grund af de også af tekniske årsager bestemte fremstillingsomkostninger kan sådanne legeringer i praksis kun anvendes til specielle formål. For-10 ståeligvis er der allerede mange gange gjort forsøg på at fremstille stållegeringer med høj sejhed og styrke på økonomisk hensigtsmæssige måder, men dette har ikke hidtil ført til nogen virkelig tilfredsstillende løsning.5 It is known to produce steel alloys, which at the same time have high toughness and strength, by using larger quantities of valuable alloy additive materials. Due to the manufacturing costs also determined for technical reasons, such alloys can in practice only be used for special purposes. Obviously, attempts have been made many times to produce high-toughness and strength steel alloys in economically appropriate ways, but this has not so far led to any truly satisfactory solution.
15 Således kendes der f.eks. højtlegerede stålmaterialer med høj styrke og sejhed med f.eks. materialenumrene 1.6357, X 2 Ni Co Mo 18 8 3, 1.6358 og 1.6359. Sådanne stålmaterialer er vanskeligt at deformere, vanskeligt at bearbejde ved hjælp af skærende værktøjer og på grund af de høje priser for legerings-20 bestanddelene også mindre økonomisk hensigtsmæssige. Der kendes også lavtlegerede stålmaterialer, såsom 75 Crl (stål-jern-liste 1975, materiale nummer 1.2003), som imidlertid ikke udviser de ønskede egenskaber med hensyn til høj sejhed og hårdhed .Thus, e.g. high alloy steel materials with high strength and toughness with e.g. material numbers 1.6357, X 2 Ni Co Mo 18 8 3, 1.6358 and 1.6359. Such steel materials are difficult to deform, difficult to process by cutting tools and, due to the high prices of the alloying components, also less economically appropriate. Also known are low alloy steel materials, such as 75 Crl (Steel Iron List 1975, material number 1.2003), which, however, do not exhibit the desired properties of high toughness and hardness.
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Det er derfor formålet med opfindelsen at tilvejebringe stållegeringer og sådanne genstande, som er billige at fremstille, og selv uafhængigt af tilstedeværelsen af betydelige andele af værdifulde legeringselementer, samtidigt udviser høj sejhed og 30 høj styrke eller besidder ekstrem høj styrke. Således skulle der være mulighed for at fremstille genstande, som anvendes i stor målestok. Det drejer sig f.eks. om boltestål eller inddrivningsbolte af traditionel form til direkte fastgørelse, og som også kan inddrives i bygningsstål med høj styrke.It is therefore an object of the invention to provide steel alloys and such articles which are inexpensive to manufacture and even independently of the presence of significant proportions of valuable alloying elements, while exhibiting high toughness and high strength or possessing extremely high strength. Thus, it should be possible to produce items that are used on a large scale. This is for example. on bolt steel or drive-in bolts of traditional form for direct attachment, and which can also be recovered in high-strength building steel.
Dette opnås ved hjælp af bainithærdbare, transformeringstræge stållegeringer med lavt martensitpunkt og genstande, som indeholder sådanne legeringer med 35 2This is accomplished by means of bainite hardenable, low martensite point transformation alloys and articles containing such alloys with 35 2
DK 155053 BDK 155053 B
0,57 - 0,75 % C0.57 - 0.75% C
0,15 - 0,35 % Si 0,70 - 0,85 % Mn0.15 - 0.35% Si 0.70 - 0.85% Mn
5 max. 0,035 % P5 max. 0.035% P
max. 0,035 % Smax. 0.035% S
0,20 - 0,50 % Mo og/eller 0,20 - 1,00 % Cr0.20 - 0.50% Mo and / or 0.20 - 1.00% Cr
Restjern og kendte forureninger, 10 hvilke stållegeringer er ejendommelige ved, at de er blevet underkastet bainithærdningen inden for temperaturområdet fra 5-50°C over martensitpunktet indtil en transformeringsgrad på fra ca. 55-85%.Residual iron and known contaminants, 10 which are steel alloys in that they have been subjected to the bainite cure within the temperature range of 5-50 ° C above the martensite point up to a degree of transformation of approx. 55-85%.
1515
Herved kan der træde 1 del Cr i stedet for hver ene del Mo.Hereby 1 part Cr may be substituted for each part Mo.
Opfindelsen er baseret på den generelle erkendelse, at stållegeringer og genstande udviser de i og for sig kontrære egen-20 skaber iform af stor sejhed pg høj styrke, når de udsættes for en kun ufuldstændig bainithærdning (varmebehandling), indtil en omdannelse eller transformering i en størrelsesorden på højst ca. 80% inden for temperaturområdet fra 5-50°C over martensitpunktet (den øvre martensitomdanne1sestempe-2 5 ratur).The invention is based on the general recognition that steel alloys and articles exhibit, in and of themselves, high tensile and high strength properties when subjected to only incomplete bainite curing (heat treatment) until a transformation or transformation into a no more than approx. 80% within the temperature range of 5-50 ° C above the martensite point (upper martensite forming temp. Temperature).
Martensitpunktet ligger for det meste i området fra ca. 180 til ca. 280°C, og især i området fra ca. 180 til 230°C, og frem for alt i området fra ca. 185 til ca. 210°C. Helt alment 30 bar det vist sig, at det over martensitpunktet værende tempera turområde, inden for hvilket den opfindelsesmæssige ufuldkomne bainithærdning kan gennemføres, er desto smallere, jo højere martensitpunktet er beliggende, og omvendt desto bredere, jo lavere martensitpunktet er beliggende. Fortrinsvis ligger 35 temperaturen for den ufuldkomne bainithærdning under ca. 270- 3The martensite point is mostly in the area from approx. 180 to approx. 280 ° C, and especially in the range of approx. 180 to 230 ° C, and above all in the range of approx. 185 to approx. 210 ° C. In general, it was found that the temperature range above the martensite point within which the inventive imperfect bainite hardening can be accomplished is the narrower, the higher the martensite point is located, and conversely the wider the lower martensite point is located. Preferably, the temperature of the imperfect bainite cure is below about 30 ° C. 270-3
DK 155053 BDK 155053 B
280°C og især ved 260°C og derunder. Særlige gunstige virkninger indtræder ved brug af stålmaterialer med martensit-punkter inden for den nedre del af det her nævnte område.280 ° C and especially at 260 ° C and below. Particularly favorable effects occur with the use of steel materials with martensite points within the lower part of the region mentioned here.
Hvis udgangsstålmaterialerne endnu ikke har den for den ufuld-5 komne bainithærdning nødvendige struktur, skal de naturligvis forbehandles på passende måde, f.eks. ved varmebehandling under dannelsen af en austenitisk struktur.Of course, if the starting steel materials do not yet have the structure necessary for the imperfect bainite hardening, they must be appropriately pretreated, e.g. by heat treatment during the formation of an austenitic structure.
Transformeringen foretages normalt op til et område'fra ca.The transformation is usually done up to an area of approx.
10 55% til ca. 85% i forhold til den dilatomensk målte, maksimale, dvs. udtømmende transformering, idet området fra 75 til 85% og især fra ca. 80% foretrækkes. Transformeringsgraden kan måleteknisk følges på enkel måde ved at udnytte den omstændighed, at bainitomdannelsen er forbundet med en direkte 15 længdeændring. Transformeringskinetikken og dermed endelig transformeringsgraden kan således følges på enkel måde ved den pågældende temperatur ved dilatomeriske målinger på stålprøver. Ved en transformeringsgrad på 80% forstår man som følge heraf 801 af den maksimale længdeændring, der opnås 20 ved fuldstændig bainitisk transformering ved den pågældende temperatur.10 55% to approx. 85% compared to the dilatomically measured, maximum, ie. exhaustive transformation, with the range from 75 to 85% and especially from approx. 80% is preferred. The degree of transformation can be monitored in a simple manner by utilizing the fact that the bainite conversion is associated with a direct length change. Thus, the transformation kinetics and thus the degree of transformation can be easily followed at that temperature by dilatomeric measurements on steel samples. As a result, a degree of transformation of 80% is understood as 801 of the maximum length change obtained 20 by complete Bainitic transformation at that temperature.
Som nævnt i tysk offentliggørelsesskrift nr. 15 58 505 er der tidligere blevet gjort forsøg på bainitisk at forbedre 2 5 legeringer med en anden sammensætning. Herved kunne der imidlertid kun opnås en forbedring af hårdheden og sejheden, hvis der foreligger en langt overvejende, f.eks. 90% eller mere, bainitisk struktur. Heraf kan der ikke sluttes, at der med legeringer med en anden specifik sammensætning kan opnås gode resultater ved at afbryde den bainitiske hærdning før tiden og det oven i købet ved en bainitisk hærdning inden for temperaturområdet fra 5-50°C over martensitpunktet.As mentioned in German Publication No. 15 58 505, attempts have been made in the past to improve Bainitic alloys with a different composition. Hereby, however, an improvement in the hardness and toughness could only be achieved if there is a far superior, e.g. 90% or more, bainitic structure. Of this, it cannot be concluded that alloys with a different specific composition can achieve good results by interrupting the bainitic curing ahead of time and, moreover, by a bainitic curing within the temperature range of 5-50 ° C above the martensite point.
Også for denne legering gælder den ovenfor nævnte transforme- 3 5 ringskarakteristik. Især viser også legeringer af denne type de nødvendige fordelagtige egenskaber, når transformeringen foretages inden for martensitdannelsens temperaturområde eller 4Also for this alloy, the above-mentioned transformation characteristic applies. In particular, alloys of this type also exhibit the necessary advantageous properties when the transformation is made within the temperature range of the martensite formation or 4
DK 155053 BDK 155053 B
inden for et temperaturområde på fra 0-50°C over martensit-punktet og indtil en transformeringsgrad på fra ca. 75 til 85¾ målt ved hjælp af den dilatomerisk bestemte transformerings-kinetik.within a temperature range of from 0-50 ° C above the martensite point and up to a degree of transformation of approx. 75 to 85¾ measured by the dilatomerically determined transformation kinetics.
55
Stållegeringerne og genstandene ifølge opfindelsen har fortrinsvis en slagsejhed, som målt på ikke med kærv forsynede runde prøver med en diamter på 4,5 mm ligger fra mere end 70 J, fortrinsvis op til 85 J og endog op til 90 J, samt en hård-10 hed på mindst 57 HRC, fortrinsvis 58 HRC og derudover op til f.eks. 60 og 61 HRC.The steel alloys and articles according to the invention preferably have an impact toughness which, measured on non-grooved round specimens with a diameter of 4.5 mm, ranges from more than 70 J, preferably up to 85 J and even up to 90 J, and a hardness. 10 at least 57 HRC, preferably 58 HRC and in addition up to e.g. 60 and 61 HRC.
Opfindelsen angår endvidere en fremgangsmåde til bainithærd-ning af genstande af transformeringstræge, bainithærdbare, 15 især lavt- eller ulegerede stållegeringer med lavt beliggende martensitomdannelsestemperatur og med 0,57 - 0,75% C, 0,15 - 0,35% Si, 0,70 - 0,85% Mn, 20 max. 0,035% P max. 0,035% S, 0,20 - 0,50% Mo og/eller 0,20 - 1,00% Cr restjern og kendte forureninger, hvilken fremgangsmåde er ejendommelig ved, at hærdningen foretages inden for temperaturområdet fra ca. 5-50°C over marten-sitpunktet og afbrydes senest ved en transformeringsgrad på ca. 55-85%, og fortrinsvis på 75-85%, målt i forhold til en 30 dilatomerisk målt maksimal transformering.The invention further relates to a method for bainite hardening of transformation funnel, bainite hardenable, especially low or unalloyed steel alloys with low lying martensite conversion temperature and with 0.57 - 0.75% C, 0.15 - 0.35% Si, O , 70 - 0.85% Mn, 20 max. 0.035% P max. 0.035% S, 0.20 - 0.50% Mo and / or 0.20 - 1.00% Cr residual iron and known contaminants, the process being characterized in that the curing is carried out within the temperature range of approx. 5-50 ° C above the mart point and is interrupted at a transformation rate of approx. 55-85%, and preferably 75-85%, measured relative to a dilatomeric measured maximum transformation.
Den eventuelle tilstedeværelse af ubetydelige mængder af legeringselementer er ikke udslagsgivende for opfindelsens fordele.The presence of insignificant amounts of alloying elements is not decisive for the advantages of the invention.
De stål legeringer ifølge opfindelsen, som også kan anvendes 35The steel alloys according to the invention which can also be used 35
DK 155053 BDK 155053 B
5 i forbindelse med fremgangsmåden, er tilstrækkeligt transformeringstræge stålmaterialer, som har de forudsætninger, der kræves for en isotermisk bainittransformering, og som så vidt muligt har lavt martensitpunkt. I det autokatalytiske net 5 fra Austin og Rickett udviser disse stalmaterialer normalt et knæk i den ellers retliniet forløbende transformeringskinetik. Der forekommer her åbenbart en udskillelse, som påvirker sejheden i ugunstig retning. Ved hjælp af den foreliggende opfindelse undgås direkte forløb, som muligvis påvirker 10 sejheden i uheldig retning, under tilvejebringelse af legeringer med høj sejhed og høj styrke.5 in connection with the process, sufficiently inert transformation materials are steel materials which have the conditions required for an isothermal bainite transformation and which have a low martensite point as far as possible. In the autocatalytic grid 5 from Austin and Rickett, these steel materials usually exhibit a break in the otherwise straight-line transformational kinetics. Evidently there is a secretion which adversely affects the toughness. By the present invention, direct processes which may adversely affect the toughness are avoided while providing high toughness and high strength alloys.
Ved hjælp af stållegeringerne ifølge opfindelsen kan der fremstilles genstande med de fordelagtige egenskaber på kendt 15 måde, især ved kolddeformering. Der kan naturligvis også fremstilles genstande af ikke-forbehandlede stållegeringer med den ovenfor nævnte stofmæssige sammensætning, og derefter kan disse genstande udsættes for den opfindelsesmæssige hærdning ^ ved passende behandling. Den væsentlige fordel ved opfindelsen ligger i denne forbindelse i, at der i modsætning til de tidligere nødvendige højtlegerede stållegeringer nu kan fremstilles produkter, der anvendes i store mængder, på økonomisk, hensigtsmæssig måde. Genstandene ifølge opfindelsen omfatter især fastgørelsesmidler (skruer, søm, bolte, især sætbolte til direkte fastgørelse, nitter, dyvler, dyveldele), værktøjer (såsom bor, boreskafter, skruetrækkere, save, stempler, dorne), maskinelementer (såsom sikringsstifter, fjedre, tallerkenfjedre, ventiler, ventilføringer, stempelringe, aksler, splitter, koblinger, skiver, lameller), militærdele (såsom våbendele, 3 0 panserplader), beslag til bygnings-, skibs-, sports- og møbelformål (såsom kæder, fiskekroge, skikanter), dele til optiske apparater og måleapparater samt halvfabrikata (såsom bånd, tråde, plader, stænger, rør og lignende).By means of the steel alloys according to the invention, articles with the advantageous properties can be prepared in known manner, especially in cold deformation. Obviously, non-pretreated steel alloys of the above-mentioned material composition can also be made and then these articles can be subjected to the inventive hardening by appropriate treatment. The main advantage of the invention in this connection lies in the fact that, contrary to the previously necessary high-alloy steel alloys, products which are used in large quantities can now be produced in an economically appropriate manner. In particular, the objects of the invention include fasteners (screws, nails, bolts, in particular direct attachment bolts, rivets, dowels, dowel parts), tools (such as drill bits, drill shanks, screwdrivers, saws, pistons, mandrels), machine elements (such as securing pins, springs, plate springs , valves, valve guides, piston rings, shafts, splits, couplings, washers, slats), military parts (such as weapon parts, armor plates), fittings for building, ship, sports and furniture purposes (such as chains, fishing hooks, ski edges), parts for optical and measuring devices and semi-finished products (such as tapes, wires, plates, rods, tubes and the like).
Opfindelsen belyses nedenfor i forbindelse med de efterfølgende eksempler.The invention is illustrated below in connection with the following examples.
3535
Claims (5)
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE2817628A DE2817628C2 (en) | 1978-04-21 | 1978-04-21 | Tough, high-strength steel alloys and processes for making such workpieces |
| DE2817628 | 1978-04-21 |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| DK162779A DK162779A (en) | 1979-10-22 |
| DK155053B true DK155053B (en) | 1989-01-30 |
| DK155053C DK155053C (en) | 1989-06-19 |
Family
ID=6037726
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| DK162779A DK155053C (en) | 1978-04-21 | 1979-04-20 | BAINITABLE, HIGH-STRENGTH TRANSFORMATION STEEL Alloy AND PREPARATION METHOD |
Country Status (22)
| Country | Link |
|---|---|
| JP (1) | JPS54141313A (en) |
| AT (1) | AT393279B (en) |
| AU (1) | AU527551B2 (en) |
| BE (1) | BE875730A (en) |
| BR (1) | BR7902454A (en) |
| CA (1) | CA1137337A (en) |
| CH (1) | CH646199A5 (en) |
| CS (1) | CS211362B2 (en) |
| DE (1) | DE2817628C2 (en) |
| DK (1) | DK155053C (en) |
| ES (1) | ES479774A1 (en) |
| FI (1) | FI69121C (en) |
| FR (1) | FR2423549B1 (en) |
| GB (1) | GB2019436B (en) |
| IT (1) | IT1112992B (en) |
| NL (1) | NL191388C (en) |
| NO (1) | NO153933C (en) |
| PL (1) | PL136257B1 (en) |
| SE (1) | SE449229B (en) |
| SU (1) | SU1232147A3 (en) |
| YU (1) | YU40746B (en) |
| ZA (1) | ZA791422B (en) |
Families Citing this family (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0020357B1 (en) * | 1978-11-15 | 1984-07-18 | Caterpillar Tractor Co. | Lower bainite alloy steel article |
| JPS5970724A (en) * | 1982-10-15 | 1984-04-21 | Seiko Instr & Electronics Ltd | Rolled hot-forged thread |
| JPS61130456A (en) * | 1984-11-29 | 1986-06-18 | Honda Motor Co Ltd | High-strength bolt and its production |
| JPH01268245A (en) * | 1988-04-19 | 1989-10-25 | Fujitsu Ltd | Changeover control circuit |
| US4960473A (en) * | 1989-10-02 | 1990-10-02 | The Goodyear Tire & Rubber Company | Process for manufacturing steel filament |
| SE510344C2 (en) * | 1997-08-01 | 1999-05-17 | Ovako Steel Ab | Way for complete bainite hardening of steel |
| NL1011806C2 (en) * | 1999-04-15 | 2000-10-17 | Skf Engineering & Res Services | Ball bearing steel with a surface with an underbainitic structure and a method of manufacturing it. |
| DE202005015611U1 (en) * | 2005-09-30 | 2005-12-29 | Textron Verbindungstechnik Gmbh & Co. Ohg | Bolts or screws with high rigidity are made from steel wire by hot rolling and cooling glowing product by blowing on air, then rolling out and cold-forming to produce head and thread |
| FR2916371B1 (en) * | 2007-05-24 | 2010-02-26 | Fwu Kuang Entpr Co Ltd | PROCESS FOR PREPARING FORGED PARTS HAVING EXCELLENT TRACTION RESISTANCE AND ELONGATION FROM STEEL MAMINERY WIRES |
| DE102008041391A1 (en) * | 2008-08-20 | 2010-01-14 | Kamax-Werke Rudolf Kellermann Gmbh & Co. Kg | High strength bolt has bainite structure produced by austempering which extends across whole cross-section of the bolt and increases its tensile strength |
| GB2485107A (en) * | 2009-08-24 | 2012-05-02 | Secr Defence | Armour |
| DE102011054840A1 (en) | 2011-10-26 | 2013-05-02 | Rud Ketten Rieger & Dietz Gmbh U. Co. Kg | Hardening steel for grade 8 and higher hoisting, lifting, tensioning and / or lashing equipment, lifting, lifting, tensioning and / or lashing equipment, and method of making such a component |
| DE102011055497A1 (en) | 2011-11-18 | 2013-05-23 | Kamax Holding Gmbh & Co. Kg | Ultra-high-strength screw with high yield ratio |
| KR101751530B1 (en) * | 2015-12-28 | 2017-06-27 | 주식회사 포스코 | Steel sheet for tool and method of manufacturing for the same |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1558505A1 (en) * | 1967-01-23 | 1970-04-16 | Hilti Ag | Anchoring means |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB517118A (en) * | 1938-07-13 | 1940-01-22 | Ver Oberschlesische Huttenwerk | Improvements in and relating to improved steels and the application thereof |
| DE973413C (en) * | 1944-05-31 | 1960-02-11 | Gussstahlwerk Witten Ag | Process to achieve a hardness of at least 54RC with high impact resistance |
| US2914401A (en) * | 1958-02-24 | 1959-11-24 | Crucible Steel Co America | Alloy steel |
| US3155550A (en) * | 1961-09-15 | 1964-11-03 | United States Steel Corp | Heat treatment of chromium-free steel bearings |
| SE342475B (en) * | 1969-03-31 | 1972-02-07 | Sandvikens Jernverks Ab |
-
1978
- 1978-04-21 DE DE2817628A patent/DE2817628C2/en not_active Expired
-
1979
- 1979-02-28 FI FI790666A patent/FI69121C/en not_active IP Right Cessation
- 1979-03-07 NL NL7901840A patent/NL191388C/en not_active IP Right Cessation
- 1979-03-15 CS CS791731A patent/CS211362B2/en unknown
- 1979-03-20 GB GB7909840A patent/GB2019436B/en not_active Expired
- 1979-03-26 ZA ZA791422A patent/ZA791422B/en unknown
- 1979-03-30 AU AU45625/79A patent/AU527551B2/en not_active Expired
- 1979-03-30 IT IT21467/79A patent/IT1112992B/en active
- 1979-04-02 AT AT2419/79A patent/AT393279B/en not_active IP Right Cessation
- 1979-04-02 CH CH305179A patent/CH646199A5/en not_active IP Right Cessation
- 1979-04-04 YU YU802/79A patent/YU40746B/en unknown
- 1979-04-12 CA CA000325474A patent/CA1137337A/en not_active Expired
- 1979-04-19 NO NO791296A patent/NO153933C/en unknown
- 1979-04-19 FR FR7909853A patent/FR2423549B1/en not_active Expired
- 1979-04-19 SE SE7903448A patent/SE449229B/en not_active IP Right Cessation
- 1979-04-20 JP JP4809679A patent/JPS54141313A/en active Granted
- 1979-04-20 PL PL1979215033A patent/PL136257B1/en unknown
- 1979-04-20 SU SU792753403A patent/SU1232147A3/en active
- 1979-04-20 BE BE0/194732A patent/BE875730A/en not_active IP Right Cessation
- 1979-04-20 DK DK162779A patent/DK155053C/en not_active IP Right Cessation
- 1979-04-20 ES ES479774A patent/ES479774A1/en not_active Expired
- 1979-04-20 BR BR7902454A patent/BR7902454A/en unknown
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1558505A1 (en) * | 1967-01-23 | 1970-04-16 | Hilti Ag | Anchoring means |
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| Date | Code | Title | Description |
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| PBP | Patent lapsed | ||
| PBP | Patent lapsed |