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Eingeladener Vortrag
- nein (3)
Der verstärkte Einsatz höherfester Stähle und Zusatzwerkstoffe erfordert ein vertieftes Verständnis der Zusammenhänge zwischen Schweißverfahren, Wärmeeinbringung, Abkühlbedingungen sowie den daraus resultierenden metallurgischen Vorgängen in der Schweißnaht und deren Umgebung. Nur aus dem Zusammenwirken aller Einflussfaktoren lassen sich Strategien ablelten, mit deren Hilfe die Festigkeitseigenschaften bzw. die Lebensdauer von Schweißkonstruktionen in einem Maße verbessert werden können, die den Einsatz höherfester Werkstoffe rechtfertigen und somit deren Leichtbaupotenzial voll ausgenutzt werden kann. Vorgestellt werden einige beispielhafte Untersuchungen an Schweißverbindungen aus höherfesten Feinkornbaustählen zu Interaktionen der Haupteinflussgrößen auf die Kaltrissbildung.
Aus wirtschaftlichen, konstruktiven sowie ästhetischen Aspekten werden moderne Stahlbaukonstruktionen immer schlanker und leichter ausgeführt. Dazu werden zunehmend höherfeste Feinkornbaustähle mit Dehngrenzen von 690 MPa bis 960 MPa in Einzelfällen bis 1100 MPa eingesetzt, Beispiele hierfür sind unter anderem die Dachkonstruktion des Sony-Centers in Berlin sowie Elemente beim Ausleger und die Tragstrukturen von Mobilkranen, die oft aus S960 oder sogar S1100 gefertigt werden, Je nach Ausnutzung der höheren Dehngrenze kann eine Gewichtsreduzierung von 30 % bis 50 % und eine Kostenersparnis von 5 % bis 15 % erreicht werden. Eine Studie der Dillinger Hütte GTS an vergleichenden Unterpulver (UP)-Schweißungen aus verschiedenen höherfesten Stählen verdeutlicht das Einsparungspotential.
In modernen Stahlkonstruktionen werden zunehmend hochfeste Feinkornbaustähle mit Streckgrenzen ab 960 MPa eingesetzt. Die wirtschaftliche Verarbeitung dieser Stähle wird neben der Erreichung der anforderungsgerechten mechanischen Eigenschaften durch die Sicherheitsanforderungen an die Schweißnaht bestimmt. Dabei bedingen hohe Eigenspannungen im Schweißnahtbereich eine Reduzierung der Bauteilsicherheit. Insbesondere bei erhöhter konstruktiver Schrumpfbehinderung können Eigenspannungen risskritisches Niveau erreichen. In einer speziellen 2- MN-Prüfanlage wurden dazu Bauteilschweißversuche mit definierter äußerer Schrumpfbehinderung abgebildet. Während dieser mehrlagigen Schweißversuche war die gleichzeitige Messung von Temperatur und Reaktionskräften beim Schweißen und Abkühlen möglich. Die schweißnahtnahen Eigenspannungen wurden mittels röntgenographischer Eigenspannungsanalyse vor und nach dem Entlasten des Probeblechs in der Prüfanlage ermittelt. Sowohl die globalen als auch die lokalen schweißbedingten Beanspruchungen waren deutlich von der Wärmeführung beeinflusst.-----------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------------
Modern steel constructions are built increasingly using highstrength fine-grained structural steels with a yield strength of ≥ 960 MPa. The efficient processing of these steels is determined not only by the achievement of the mechanical properties needed but also by the safety requirements of the weld. High stresses in the weld area cause a reduction of the component safety. Residual stresses can reach a critical level at which the material is susceptible to cracking, especially in case of increased constructive restraint. For this purpose, component weld tests with a defined external restraint were reproduced in a special 2-MN-testing facility. During these multi-layer weld tests the simultaneous measurement of the temperature and reaction forces during welding and cooling was possible. The residual stresses of the weld joint area were determined by means of X-ray difraction analysis before and after release of the restraint. The global stresses due to welding as well as the local ones were clearly influenced by the heat control.
Innovative low transformation temperature (LTT) welding filler materials are featuring a characteristic chemical composition which favors the formation of martensite at comparatively low temperatures. This permits deliberate adjustment of welding residual stresses. Even though numerous investigations can be found in the literature on this issue, they provide only little insight into the interaction between phase transformation and resulting welding residual stresses. For this purpose, a component weld test was performed in a special large-scale testing facility. The results illustrate that the desired residual stress control by using LTT alloys is actually feasible. With increasing shrinkage restraint, however, higher tensile residual stresses are formed in transverse direction of the weld. By contrast, the residual stress level in longitudinal weld direction is nearly independent of the restraint conditions. On-line stress analysis revealed that the amount of stress reduction during cooling of the individual weld runs is dependent on the weld volume undergoing phase transformation. Overall, evidence was furnished that the approach of residual stress engineering by LTT alloys is suitable even in the case of large-scale multilayer welding.
Correlating welding reaction stresses and weld process conditons for high-strength steel S960QL
(2014)
As a result of current trends towards lightweight design, a growing amount of high-strength steels with yield strengths above 690 MPa is applied. In comparison to the weld process of lower-strength steels, small working ranges have to be achieved with respect to a special microstructure and high yield ratio. However, the sustainable and economic application of these steels depends on the loading capacity and the safety of welds when designing weld constructions. For these demands, a precise knowledge of welding stress level and distribution is essential. Therefore, the present study is concerned with the interaction between heat control (interpass temperature and heat input) and local as well as global stresses in high-strength steel welds. Specimens were multirun welded under defined restraint conditions in a special test facility (controlled tensile weldability (CTW) test) to consider global restraint. For the comparison concerning local residual stresses, free shrinkage test welds were performed as well. The evaluation shows a significant influence of the interpass temperature on the global reaction forces. Furthermore, increased heat input and high interpass temperatures cause higher tensile residual stresses. This occurred in the weld area of both free shrinkage test specimen and CTW test specimen.
The increased application of higher-strength steels and filler materials necessitates more profound understanding of the interaction between the welding process, the heat input, the cooling conditions and the resulting metallurgical processes in the weld and its surroundings. Strategies which help to improve the strength properties and life-time of welded structures to such an extent that the utilisation of higher-strength materials can be justified and their lightweight construction potential can thus be exploited to the full can only be derived from the interaction between all the influencing factors. Examples of a few investigations on welded joints between higher-strength fine-grained structural steels with regard to the interactions between the main variables influencing the cold cracking are presented in this article.
The roles of microalloying niobium, titanium and vanadium for controlling austenite grain growth, microstructure evolution and hardness were investigated at different simulated heat affected zones (HAZ) for high strength low alloy (HSLA) S690QL steel. High resolution FEG-SEM has been used to characterize fine bainitic ferrite, martensite and nanosized second phases at simulated coarse and fine grain HAZs. It was found that for Ti bearing steel (Ti/N ratio is 2) austenite grain had the slowest growth rate due to the presence of most stable TiN. The fine cuboidal particles promoted intragranular acicular ferrite (IGF) formation. Nb bearing steel exhibited relatively weaker grain growth retardation compared with titanium bearing steels and a mixed microstructure of bainite and martensite was present for all simulated HAZs. IGF existed at coarse grain HAZ of Ti+V bearing steel but it was totally replaced by bainite at fine grain HAZs. Hardness result was closely related to the morphology of bainitic ferrite, intragranular ferrite and second phases within ferrite. The microstructure and hardness results of different simulated HAZs were in good agreement with welded experimental results.